Magnetic recording medium and magnetic recording and reproducing device

ABSTRACT

Provided are a magnetic recording medium, in which a magnetic layer includes a ferromagnetic hexagonal ferrite powder, a binding agent, an oxide abrasive, an intensity ratio Int(110)/Int(114) obtained by an X-ray diffraction analysis of the magnetic layer by using an In-Plane method is 0.5 to 4.0, a vertical squareness ratio is 0.65 to 1.00, one or more kinds of component selected from the group consisting of fatty acid and fatty acid amide is contained in a magnetic layer side portion on the non-magnetic support, a C—H derived C concentration of the magnetic layer is 45 atom % to 65 atom %, and an average particle diameter of the oxide abrasive obtained from a secondary ion image obtained by irradiating the surface of the magnetic layer with a focused ion beam is 0.04 μm to 0.08 μm, and a magnetic recording and reproducing device including this magnetic recording medium.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application claims priority under 35 U.S.C 119 to Japanese Patent Application No. 2017-191664 filed on Sep. 29, 2017 and Japanese Patent Application No. 2018-170191 filed on Sep. 12, 2018. Each of the above applications is hereby expressly incorporated by reference, in its entirety, into the present application.

BACKGROUND OF THE INVENTION 1. Field of the Invention

The present invention relates to a magnetic recording medium and a magnetic recording and reproducing device.

2. Description of the Related Art

The recording and/or reproducing of information with respect to a magnetic recording medium is generally performed by bringing a surface of a magnetic recording medium (surface of magnetic layer) into contact with a magnetic head (hereinafter, also referred to as a “head”) and sliding.

One performance required from the magnetic recording medium is to exhibit excellent electromagnetic conversion characteristics in a case of reproducing information recorded on the magnetic recording medium.

Meanwhile, in a case where chipping of a reproducing element of the head occurs due to the sliding between the surface of the magnetic layer and the head (hereinafter, also referred to as “head element chipping”), a distance between the surface of the magnetic layer and the reproducing element increases and spacing loss which is a reason of a deterioration of electromagnetic conversion characteristics may occur. As the countermeasure for preventing the occurrence of this spacing loss, a technology of providing a protective layer on the head has been proposed in the related art (for example, see JP2005-92967A).

SUMMARY OF THE INVENTION

However, data recorded on various recording media such as a magnetic recording medium is called hot data, warm data, and cold data depending on access frequencies (reproducing frequencies). The access frequencies decrease in the order of hot data, warm data, and cold data, and it is general that the cold data is stored as being recorded on a recording medium for a long period of time which is longer than 10 years (for example, several tens of years). The recording and storing of the cold data as described above is referred to as “archive”. The data amount of the cold data recorded and stored on a magnetic recording medium increases in accordance with a dramatic increase in information contents and digitization of various information in recent years, and accordingly, a magnetic recording and reproducing system suitable for the archive is gaining attention.

In such a circumstance, a green tape test (GTT) is performed as a test for a magnetic recording and reproducing device (generally referred to as a “drive”). In the GTT, a particular use aspect for archive, in which cold data having a low access frequency is recorded and reproducing, is assumed, and a plurality of (for example, several hundreds of) new (unused) magnetic recording media are slid with respect to one head while changing the magnetic recording media. Meanwhile, in a head durability test in the related art, a use aspect with a high access frequency compared to the archive purpose has been assumed, and accordingly, one magnetic recording medium is normally repeatedly slid on the same magnetic head, without changing the magnetic recording medium to a new product. In such a durability test in the related art, a surface of a magnetic layer is worn while repeating the sliding, and thus, the head element chipping gradually becomes to hardly occur. With respect to this, in the GTT, the same head is repeatedly slid on a plurality of new magnetic recording media by changing the magnetic recording medium slid on the head to a new product, and thus, the head is in a severe condition where the chipping significantly easily occurs, compared to the durability test in the related art. In order to prevent such head element chipping in the GTT, the countermeasure on the head side and the countermeasure on the magnetic recording medium side have been considered. For example, as the countermeasure on the head side, an increase in thickness of a protective layer of the head has been considered, but an increase in thickness of the protective layer of the head causes an increase in distance between the surface of the magnetic layer and the reproducing element of the head, and this may cause spacing loss. With respect to this, in a case where the countermeasure on the magnetic recording medium side for preventing the head element chipping in the GTT can be found, a magnetic recording medium with such a countermeasure may be a magnetic recording medium suitable for a recording medium for archive, in which head element chipping hardly occurs in a use aspect for archive.

Therefore, an aspect of the invention provides for a magnetic recording medium suitable for a recording medium for archive capable of exhibiting excellent electromagnetic conversion characteristics, specifically, a magnetic recording medium capable of exhibiting excellent electromagnetic conversion characteristics and preventing occurrence of head element chipping in a green tape test (GTT).

According to an aspect of the invention, there is provided a magnetic recording medium comprising: a non-magnetic support; and a magnetic layer, in which the magnetic layer contains a ferromagnetic powder, a binding agent and an oxide abrasive, the ferromagnetic powder is a ferromagnetic hexagonal ferrite powder, an intensity ratio (Int(110)/Int(114); hereinafter, also referred to as “X-ray diffraction (XRD) intensity ratio) of a peak intensity Int(110) of a diffraction peak of a (110) plane with respect to a peak intensity Int(114) of a diffraction peak of a (114) plane of a hexagonal ferrite crystal structure obtained by an X-ray diffraction analysis of the magnetic layer by using an In-Plane method is 0.5 to 4.0, a vertical squareness ratio of the magnetic recording medium is 0.65 to 1.00, one or more kinds of component selected from the group consisting of fatty acid and fatty acid amide is contained in a magnetic layer side portion on the non-magnetic support, a C—H derived C concentration calculated from a C—H peak area ratio of C1s spectra obtained by X-ray photoelectron spectroscopic analysis performed on the surface of the magnetic layer at a photoelectron take-off angle of 10 degrees (hereinafter, also simply referred to as a “C—H derived C concentration of magnetic layer” or simply a “C—H derived C concentration”) is 45 atom % to 65 atom %, and an average particle diameter of the oxide abrasive obtained from a secondary ion image obtained by irradiating the surface of the magnetic layer with a focused ion beam (FIB) (hereinafter, also referred to as a “FIB abrasive diameter”) is 0.04 μm to 0.08 μm.

In one aspect, the vertical squareness ratio may be 0.65 to 0.90.

In one aspect, the oxide abrasive may be an alumina powder.

In one aspect, the magnetic recording medium may further comprise a non-magnetic layer including a non-magnetic powder and a binding agent between the non-magnetic support and the magnetic layer.

In one aspect, the magnetic recording medium may further comprise a back coating layer including a non-magnetic powder and a binding agent on a surface of the non-magnetic support opposite to a surface provided with the magnetic layer.

In one aspect, the magnetic recording medium may be a magnetic tape.

According to another aspect of the invention, there is provided a magnetic recording and reproducing device comprising: the magnetic recording medium; and a magnetic head.

In one aspect, the magnetic head may be a magnetic head including magnetoresistive (MR) element.

According to one aspect of the invention, it is possible to provide a magnetic recording medium suitable for archive use, which is capable of exhibiting excellent electromagnetic conversion characteristics and preventing occurrence of head element chipping in a green tape test (GTT), and a magnetic recording and reproducing device including this magnetic recording medium.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 shows an example (step schematic view) of a specific aspect of a magnetic tape manufacturing step.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

Magnetic Recording Medium

One aspect of the invention relates to a magnetic recording medium including: a non-magnetic support; and a magnetic layer, in which the magnetic layer contains a ferromagnetic powder, a binding agent and an oxide abrasive, the ferromagnetic powder is a ferromagnetic hexagonal ferrite powder, an intensity ratio (Int(110)/Int(114)) of a peak intensity Int(110) of a diffraction peak of a (110) plane with respect to a peak intensity Int(114) of a diffraction peak of a (114) plane of a hexagonal ferrite crystal structure obtained by an X-ray diffraction analysis of the magnetic layer by using an In-Plane method is 0.5 to 4.0, a vertical squareness ratio of the magnetic recording medium is 0.65 to 1.00, one or more kinds of component selected from the group consisting of fatty acid and fatty acid amide is contained in a magnetic layer side portion on the non-magnetic support, a C—H derived C concentration calculated from a C—H peak area ratio of C1s spectra obtained by X-ray photoelectron spectroscopic analysis performed on the surface of the magnetic layer at a photoelectron take-off angle of 10 degrees is 45 atom % to 65 atom %, and an average particle diameter of the oxide abrasive obtained from a secondary ion image obtained by irradiating the surface of the magnetic layer with a focused ion beam (FIB abrasive diameter) is 0.04 μm to 0.08 μm.

In the invention and the specification, the “surface of the magnetic layer” is identical to the surface of the magnetic recording medium on the magnetic layer side. In the invention and the specification, the “ferromagnetic hexagonal ferrite powder” means an aggregate of a plurality of ferromagnetic hexagonal ferrite particles. The ferromagnetic hexagonal ferrite particles are ferromagnetic particles having a hexagonal ferrite crystal structure. Hereinafter, particles (ferromagnetic hexagonal ferrite particles) configuring the ferromagnetic hexagonal ferrite powder are also referred to as “hexagonal ferrite particles” or simply “particles”. The “aggregate” not only includes an aspect in which particles configuring the aggregate are directly in contact with each other, but also includes an aspect in which a binding agent or an additive is interposed between the particles. The points described above are also applied to various powders such as non-magnetic powder of the invention and the specification, in the same manner.

The aforementioned magnetic recording medium contains one or more kinds of components selected from the group consisting of fatty acid and fatty acid amide in a magnetic layer side portion on the non-magnetic support. In the invention and the specification, the “magnetic layer side portion on the non-magnetic support” is a magnetic layer, with regard to the magnetic recording medium having the magnetic layer directly on the non-magnetic support. The “magnetic layer side portion on the non-magnetic support” is a magnetic layer and/or a non-magnetic layer, with regard to the magnetic recording medium having a non-magnetic layer described further below between a non-magnetic support and a magnetic layer. Hereinafter, the “magnetic layer side portion on the non-magnetic support” may be simply referred to as the “magnetic layer side portion”.

In the invention and the specification, the “oxide abrasive” means a non-magnetic oxide powder having Mohs hardness exceeding 8.

In the invention and the specification, the description regarding directions and angles (for example, vertical, orthogonal, parallel, and the like) includes a range of errors allowed in the technical field of the invention, unless otherwise noted. For example, the range of errors means a range of less than ±10° from an exact angle, and is preferably within ±5° and more preferably within ±3° from an exact angle.

A surmise of the inventors regarding the magnetic recording medium is as follows.

The inventors have thought that the vertical squareness ratio of the magnetic recording medium and the XRD intensity ratio set to be in the ranges described above mainly contribute to the magnetic recording medium to exhibit excellent electromagnetic conversion characteristics, specifically to reproduce information recorded on the magnetic recording medium at a high signal-to-noise-ratio (SNR). This point will be further described hereinafter.

The magnetic recording medium includes the ferromagnetic hexagonal ferrite powder in the magnetic layer. The inventors have surmised that the ferromagnetic hexagonal ferrite powder included in the magnetic layer includes particles which affects magnetic properties of the ferromagnetic hexagonal ferrite powder (aggregate of particles) (hereinafter, also referred to as “former particles”) and particles which are considered not to affect or slightly affects the magnetic properties thereof (hereinafter, also referred to as “latter particles”). It is considered that the latter particles are, for example, fine particles generated due to partial chipping of particles due to a dispersion process performed at the time of preparing a magnetic layer forming composition.

The inventors have thought that, in the particles included in the ferromagnetic hexagonal ferrite powder included in the magnetic layer, the former particles are particles causing the diffraction peak in the X-ray diffraction analysis using the In-Plane method, and since the latter particles are fine, the latter particles do not cause the diffraction peak or hardly affect the diffraction peak. Accordingly, it is surmised that it is possible to control a presence state of the particles affecting the magnetic properties of the ferromagnetic hexagonal ferrite powder present in the magnetic layer, based on the intensity of the diffraction peak caused by the X-ray diffraction analysis of the magnetic layer using the In-Plane method. The inventors have surmised that the XRD intensity ratio which will be described later in detail is an index regarding this point.

Meanwhile, the vertical squareness ratio is a ratio of residual magnetization with respect to saturation magnetization measured in a direction vertical to the surface of the magnetic layer and this value decreases, as a value of the residual magnetization decreases. It is surmised that, since the latter particles are fine and hardly hold magnetization, as a large amount of the latter particles is included in the magnetic layer, the vertical squareness ratio tends to decrease. Accordingly, the inventors have thought that the vertical squareness ratio may be an index for the amount of the latter particles (fine particles) present in the magnetic layer. In addition, the inventors have thought that, as the amount of such fine particles present in the magnetic layer is small, the magnetic properties of the ferromagnetic hexagonal ferrite powder are improved.

In addition, the inventors have surmised that it is possible to improve electromagnetic conversion characteristics, by setting the vertical squareness ratio of the magnetic recording medium and the XRD intensity ratio to be in the ranges described above, by decreasing the amount of latter particles (fine particles) present in the magnetic layer and controlling the state of the former particles present in the magnetic layer.

Further, the inventors have thought that, the C—H derived C concentration of the magnetic layer and the FIB abrasive diameter in the magnetic recording medium set to be in the respective ranges described above mainly contribute to prevention of occurrence of the head element chipping in the GTT. This point will be further described hereinafter.

The “X-ray photoelectron spectroscopic analysis” is an analysis method which is normally called Electron Spectroscopy for Chemical Analysis (ESCA) or X-ray Photoelectron Spectroscopy (XPS). Hereinafter, the X-ray photoelectron spectroscopic analysis is also referred to as ESCA. The ESCA is an analysis method using a phenomenon of photoelectron emission in a case where a surface of a measurement target sample is irradiated with X-ray, and is widely used as an analysis method regarding a surface portion of a measurement target sample. According to the ESCA, it is possible to perform qualitative analysis and quantitative analysis by using X-ray photoemission spectra acquired by the analysis regarding the sample surface of the measurement target. A depth from the sample surface to the analysis position (hereinafter, also referred to as a “detection depth”) and photoelectron take-off angle generally satisfy the following expression: detection depth≈mean free path of electrons×3×sin θ. In the expression, the detection depth is a depth where 95% of photoelectrons configuring X-ray photoemission spectra are generated, and θ is the photoelectron take-off angle. From the expression described above, it is found that, as the photoelectron take-off angle decreases, the analysis regarding a shallow part of the depth from the sample surface can be performed, and as the photoelectron take-off angle increases, the analysis regarding a deep part of the depth from the sample surface can be performed. In the analysis performed by the ESCA at a photoelectron take-off angle of 10 degrees, an extreme outermost surface portion having a depth of approximately several nm from the sample surface generally becomes an analysis position. Accordingly, in the surface of the magnetic layer of the magnetic recording medium, according to the analysis performed by the ESCA at a photoelectron take-off angle of 10 degrees, it is possible to perform composition analysis regarding the extreme outermost surface portion having a depth of approximately several nm from the surface of the magnetic layer.

The C—H derived C concentration is a proportion of carbon atoms C configuring the C—H bond occupying total (based on atom) 100 atom % of all elements detected by the qualitative analysis performed by the ESCA. The magnetic recording medium includes one or more components selected from the group consisting of fatty acid and fatty acid amide in the magnetic layer side portion. Fatty acid and fatty acid amide are components which can respectively function as a lubricant in the magnetic recording medium. The inventors have thought that, the C—H derived C concentration obtained by the analysis performed on the surface of the magnetic layer of the magnetic recording medium including one or more of these components in the magnetic layer side portion, by the ESCA at a photoelectron take-off angle of 10 degrees becomes an index for the presence amount of the components (one or more components selected from the group consisting of fatty acid and fatty acid amide) in the extreme outermost surface portion of the magnetic layer. Specific description is as follows.

In X-ray photoemission spectra (horizontal axis: bonding energy, vertical axis: strength) obtained by the analysis performed by the ESCA, the C1s spectra include information regarding an energy peak of a 1 s orbit of the carbon atoms C. In such C1s spectra, a peak positioned at the vicinity of the bonding energy 284.6 eV is a C—H peak. This C—H peak is a peak derived from the bonding energy of the C—H bond of the organic compound. The inventors have surmised that, in the extreme outermost surface portion of the magnetic layer in the magnetic recording medium, which contains one or more components selected from the group consisting of fatty acid and fatty acid amide in the magnetic layer side portion on the non-magnetic support (in other words, in the magnetic recording medium in which one or more kinds of components selected from the group consisting of fatty acid and fatty acid amide is detected from the magnetic layer side portion on the non-magnetic support), main constituent components of the C—H peak are components selected from the group consisting of fatty acid and fatty acid amide. Accordingly, the inventors have thought that the C—H derived C concentration can be an index for the presence amount of the components as described above.

The inventors have thought that a state where the C—H derived C concentration is 45 atom % to 65 atom %, that is, a state where a large amount of one or more components selected from the group consisting of fatty acid and fatty acid amide is present in the extreme outermost surface portion of the magnetic layer contribute to the promoting of the smooth sliding between the surface of the magnetic layer and the head (improvement of sliding properties). The inventors have surmised that, in a case where the sliding properties are improved, it is possible to prevent chipping of the head element due to the sliding with the surface of the magnetic layer in the GTT. In addition, it is surmised that, in a case where the surface of the magnetic layer and the head are extremely smoothly slid on each other, slipping occurs, and it is thought that this also causes the occurrence of head element chipping in the GTT. With respect to this, the inventors have surmised that, in a case where the C—H derived C concentration is equal to or greater than 65 atom %, it is possible to prevent occurrence of slipping and to prevent occurrence of the head element chipping in the GTT due to the slipping.

In the invention and the specification, the FIB abrasive diameter is a value obtained by the following method.

(1) Obtaining Secondary Ion Image

A secondary ion image of a region, having a size of 25 μm×25 μm, of the surface of the magnetic layer of the magnetic recording medium which is a target for obtaining the FIB abrasive diameter is obtained by a focused ion beam device. As the focused ion beam device, MI4050 manufactured by Hitachi High-Technologies Corporation can be used.

Beam irradiation conditions of the focused ion beam device in a case of obtaining the secondary ion image are set so that an acceleration voltage is 30 kV, a current value is 133 pA (picoampere), a beam size is 30 nm, and a brightness is 50%. A coating process with respect to a surface of a magnetic layer before the imaging is not performed. A secondary ion (SI) signal is detected by a secondary ion detector and a secondary ion image is captured. Conditions for capturing a secondary ion image are determined by the following method. ACB (auto contrast brightness) is carried out at three spots on a non-imaged region of the surface of the magnetic layer (i.e., ACB is carried out three times) to stabilize a color of the image. Then, the contrast reference value and the brightness reference value are determined. The brightness reference value as determined in the above ACB and the contrast value which is lowered by 1% from the contrast reference value as determined in the above ACB are determined as the conditions for capturing a secondary ion image. An non-imaged region of the surface of the magnetic layer is selected, and a secondary ion image is captured under the conditions for capturing as determined above. A portion for displaying a size and the like (micron bar, cross mark, and the like) is removed from the captured image, and a secondary ion image having the pixel number of 2,000 pixel×2,000 pixel is obtained. For specific examples of the imaging conditions, examples which will be described later can be referred to.

(2) Calculation of FIB Abrasive Diameter

The secondary ion image obtained in (1) is put into image processing software, and a binarization process is performed by the following procedure. As the image analysis software, ImageJ which is free software can be used, for example.

A tone of the secondary ion image obtained in (1) is changed to 8 bit. Regarding threshold values for the binarization process, a lower limit value is set as 250 gradations, an upper limit value is set as 255 gradations, and the binarization process is executed by these two threshold values. After the binarization process, a noise component removal process is performed by the image analysis software. The noise component removal process can be carried out, for example, by the following method. On the image analysis software, ImageJ, a noise cut process Despeckle is selected, and Size 4.0-infinity is set on AnalyzeParticle to remove noise components.

Each white-shining portion in the binarization process image obtained as described above is determined as an oxide abrasive, and the number of white-shining portions is obtained by the image analysis software, and the area of the white-shining portion is obtained. An equivalent circle diameter of each portion is obtained from the area of the white-shining portion obtained here. Specifically, an equivalent circle diameter L is calculated from the obtained area A by (A/π)̂(½)×2=L.

The above step is performed four times at different portions (25 μm×25 μm) of the surface of the magnetic layer of the magnetic recording medium which is a target for obtaining the FIB abrasive diameter, and the FIB abrasive diameter is calculated from the obtained results by an expression; FIB abrasive diameter=Σ(Li)/Σi. Σi is a total number of the white-shining portions observed in the binarization process image obtained by performing the above step four times. Σ(Li) is a total of the equivalent circle diameters L obtained regarding the white-shining portions observed in the binarization process image obtained by performing the above step four times. Regarding the white-shining portion, only a part of the portion may be included in the binarization process image. In such a case, Σi and Σ(Li) are obtained without including the part.

The FIB abrasive diameter is a value which can be an index of a presence state of an oxide abrasive in the magnetic layer, and is obtained from the secondary ion image obtained by irradiating the surface of the magnetic layer with a focused ion beam (FIB). This secondary ion image is generated by capturing secondary ion generated from the surface of the magnetic layer irradiated with the FIB. Meanwhile, as an observation method of the presence state of the abrasive in the magnetic layer, a method using a scanning electron microscope (SEM) has been proposed in the related art. By the SEM, the surface of the magnetic layer is irradiated with an electron beam and secondary electrons emitted from the surface of the magnetic layer are captured to generate an image (SEM image). Even in a case where the same magnetic layer is observed, a size of the oxide abrasive obtained from the secondary ion image and a size of the oxide abrasive obtained from the SEM image are different from each other due to a difference of such image generation principle. As a result of intensive studies of the inventors, a presence state of the oxide abrasive in the magnetic layer is controlled so that the FIB abrasive diameter becomes 0.04 μm to 0.08 μm, by setting the FIB abrasive diameter obtained from the secondary ion image by the method described above as a new index of the presence state of the oxide abrasive in the magnetic layer. The inventors have thought that the controlling of the presence state of the oxide abrasive in the magnetic layer as described above also contributes to prevention of chipping of the head element due to the sliding on the surface of the magnetic layer in the GTT.

The inventors have surmised that, as described above, excellent electromagnetic conversion characteristics exhibited by the magnetic recording medium mainly contributes to the setting of the XRD intensity ratio and the vertical squareness ratio to be in the ranges described above, and the prevention of the occurrence of the head element chipping in the GTT mainly contributes to the setting of the C—H derived C concentration of the magnetic layer and the FIB abrasive diameter to be in the ranges described above. However, the invention is not limited to the surmise described above.

Hereinafter, the magnetic recording medium will be further described in detail.

XRD Intensity Ratio

The magnetic recording medium includes ferromagnetic hexagonal ferrite powder in the magnetic layer. The XRD intensity ratio is obtained by the X-ray diffraction analysis of the magnetic layer including the ferromagnetic hexagonal ferrite powder by using the In-Plane method. Hereinafter, the X-ray diffraction analysis performed by using the In-Plane method is also referred to as “In-Plane XRD”. The In-Plane XRD is performed by irradiating the surface of the magnetic layer with the X-ray by using a thin film X-ray diffraction device under the following conditions. The magnetic recording medium is widely divided into a tape-shaped magnetic recording medium (magnetic tape) and a disk-shaped magnetic recording medium (magnetic disk). A measurement direction is a longitudinal direction of the magnetic tape and a radius direction of the magnetic disk.

Cu ray source used (output of 45 kV, 200 mA)

Scan conditions: 0.05 degree/step, 0.1 degree/min in a range of 20 to 40 degrees

Optical system used: parallel optical system

Measurement method: 2θχ scan (X-ray incidence angle of 0.25°)

The values of the conditions are set values of the thin film X-ray diffraction device. As the thin film X-ray diffraction device, a well-known device can be used. As an example of the thin film X-ray diffraction device, Smart Lab manufactured by Rigaku Corporation. A sample to be subjected to the In-Plane XRD analysis is a medium sample cut out from the magnetic recording medium which is a measurement target, and the size and the shape thereof are not limited, as long as the diffraction peak which will be described later can be confirmed.

As a method of the X-ray diffraction analysis, thin film X-ray diffraction and powder X-ray diffraction are used. In the powder X-ray diffraction, the X-ray diffraction of the powder sample is measured, whereas, according to the thin film X-ray diffraction, the X-ray diffraction of a layer or the like formed on a substrate can be measured. The thin film X-ray diffraction is classified into the In-Plane method and an Out-Of-Plane method. The X-ray incidence angle at the time of the measurement is 5.00° to 90.00° in a case of the Out-Of-Plane method, and is generally 0.20° to 0.50°, in a case of the In-Plane method. In the In-Plane XRD of the invention and the specification, the X-ray incidence angle is 0.25° as described above. In the In-Plane method, the X-ray incidence angle is smaller than that in the Out-Of-Plane method, and thus, a depth of penetration of the X-ray is shallow. Accordingly, according to the X-ray diffraction analysis by using the In-Plane method (In-Plane XRD), it is possible to perform the X-ray diffraction analysis of a surface portion of a measurement target sample. Regarding the magnetic recording medium sample, according to the In-Plane XRD, it is possible to perform the X-ray diffraction analysis of the magnetic layer. The XRD intensity ratio is an intensity ratio (Int(110)/Int(114)) of a peak intensity Int(110) of a diffraction peak of a (110) plane with respect to a peak intensity Int(114) of a diffraction peak of a (114) plane of a hexagonal ferrite crystal structure, in X-ray diffraction spectra obtained by the In-Plane XRD. The term Int is used as abbreviation of intensity. In the X-ray diffraction spectra obtained by In-Plane XRD (vertical axis: intensity, horizontal axis: diffraction angle 2θχ (degree)), the diffraction peak of the (114) plane is a peak at which the 2θχ is detected at 33 to 36 degrees, and the diffraction peak of the (110) plane is a peak at which the 2θχ is detected at 29 to 32 degrees.

Among the diffraction plane, the (114) plane having a hexagonal ferrite crystal structure is positioned close to particles of the ferromagnetic hexagonal ferrite powder (hexagonal ferrite particles) in an easy-magnetization axial direction (c axis direction). In addition the (110) plane having a hexagonal ferrite crystal structure is positioned in a direction orthogonal to the easy-magnetization axial direction.

The inventors have surmised that, in the X-ray diffraction spectra obtained by the In-Plane XRD, as the intensity ratio (Int(110)/Int(114); XRD intensity ratio) of the peak intensity Int(110) of the diffraction peak of a (110) plane with respect to the peak intensity Int(114) of the diffraction peak of the (114) plane of a hexagonal ferrite crystal structure increases, a large number of the former particles present in a state where a direction orthogonal to the easy-magnetization axial direction is closer to a parallel state with respect to the surface of the magnetic layer is present in the magnetic layer, and as the XRD intensity ratio decreases, a small amount of the former particles present in such a state is present in the magnetic layer. It is thought that a state where the XRD intensity ratio is 0.5 to 4.0 means a state where the former particles are suitably aligned in the magnetic layer. The inventors have surmised that this contributes to the improvement of electromagnetic conversion characteristics.

The XRD intensity ratio is preferably equal to or smaller than 3.5 and more preferably equal to or smaller than 3.0, from a viewpoint of further improving electromagnetic conversion characteristics. From the same viewpoint, the XRD intensity ratio is preferably equal to or greater than 0.7 and more preferably equal to or greater than 1.0. The XRD intensity ratio can be, for example, controlled in accordance with process conditions of an alignment process performed in a manufacturing step of the magnetic recording medium. As the alignment process, the homeotropic alignment process is preferably performed. The homeotropic alignment process can be preferably performed by applying a magnetic field vertically to the surface of a coating layer of a magnetic layer forming composition in a wet state (undried state). As the alignment conditions are reinforced, the value of the XRD intensity ratio tends to increase. As the process conditions of the alignment process, magnetic field strength of the alignment process is used. The process conditions of the alignment process are not particularly limited. The process conditions of the alignment process may be set so as that the XRD intensity ratio of 0.5 to 4.0 can be realized. As an example, the magnetic field strength of the homeotropic alignment process can be 0.10 to 0.80 T or 0.10 to 0.60 T. As dispersibility of the ferromagnetic hexagonal ferrite powder in the magnetic layer forming composition increases, the value of the XRD intensity ratio tends to increase by the homeotropic alignment process.

Vertical Squareness Ratio

The vertical squareness ratio is a squareness ratio measured regarding a magnetic recording medium in a vertical direction. The “vertical direction” described regarding the squareness ratio is a direction orthogonal to the surface of the magnetic layer. For example, in a case where the magnetic recording medium is a tape-shaped magnetic recording medium, that is, a magnetic tape, the vertical direction is a direction orthogonal to a longitudinal direction of the magnetic tape. The vertical squareness ratio is measured by using a vibrating sample magnetometer. Specifically, the vertical squareness ratio of the invention and the specification is a value obtained by sweeping an external magnetic field in the magnetic recording medium at a measurement temperature of 23° C.±1° C. in the vibrating sample magnetometer, under conditions of a maximum external magnetic field of 1194 kA/m (15 kOe) and a scan speed of 4.8 kA/m/sec (60 Oe/sec), and is a value after diamagnetic field correction. The measurement value is obtained as a value obtained by subtracting magnetization of a sample probe of the vibrating sample magnetometer as background noise.

The vertical squareness ratio of the magnetic recording medium is equal to or greater than 0.65. The inventors have surmised that the vertical squareness ratio of the magnetic recording medium is an index for the presence amount of the latter particles (fine particles) described above. It is thought that, in the magnetic layer in which the vertical squareness ratio of the magnetic recording medium is equal to or greater than 0.65, the presence amount of such fine particles is small. The inventors have surmised that this contributes to the improvement of electromagnetic conversion characteristics. From a viewpoint of further improving electromagnetic conversion characteristics, the vertical squareness ratio is preferably equal to or greater than 0.70, more preferably equal to or greater than 0.73, and even more preferably equal to or greater than 0.75. In addition, in principle, a maximum value of the squareness ratio is 1.00. Accordingly, the vertical squareness ratio of the magnetic tape is equal to or smaller than 1.00. The vertical squareness ratio may be, for example, equal to or smaller than 0.95, equal to or smaller than 0.90, equal to or smaller than 0.87, or equal to or smaller than 0.85. However, it is thought that, a great value of the vertical squareness ratio is preferable, from a viewpoint of decreasing the amount of the fine latter particles in the magnetic layer and improving electromagnetic conversion characteristics. Therefore, the vertical squareness ratio may be greater than the value exemplified above.

The inventors have considered that, in order to set the vertical squareness ratio to be equal to or greater than 0.65, it is preferable to prevent occurrence of fine particles due to partial chipping of the particles in a preparation step of the magnetic layer forming composition. A specific means for preventing the occurrence of chipping will be described later.

C—H Derived C Concentration

The C—H derived C concentration of the magnetic recording medium is 45 atom % to 65 atom %. From a viewpoint of further preventing the occurrence of the head element chipping in the GTT, the C—H derived C concentration is preferably equal to or greater than 48 atom % and more preferably equal to or greater than 50 atom %. In addition, from the same viewpoint, the C—H derived C concentration is preferably equal to or smaller than 63 atom % and more preferably equal to or smaller than 60 atom %.

As described above, the C—H derived C concentration is a value obtained by analysis using ESCA. A region for the analysis is a region having an area of 300 μm×700 μm at a random position of the surface of the magnetic layer of the magnetic recording medium. The qualitative analysis is performed by wide scan measurement (pass energy: 160 eV, scan range: 0 to 1,200 eV, energy resolution: 1 eV/step) performed by ESCA. Then, spectra of entirety of elements detected by the qualitative analysis are obtained by narrow scan measurement (pass energy: 80 eV, energy resolution: 0.1 eV, scan range: set for each element so that the entirety of spectra to be measured is included). An atomic concentration (unit: atom %) of each element is calculated from the peak area of each spectrum obtained as described above. Here, an atomic concentration (C concentration) of carbon atoms is also calculated from the peak area of C1s spectra.

In addition, C1s spectra are obtained (pass energy: 10 eV, scan range: 276 to 296 eV, energy resolution: 0.1 eV/step). The obtained C1s spectra are subjected to a fitting process by a nonlinear least-squares method using a Gauss-Lorentz complex function (Gaussian component: 70%, Lorentz component: 30%), peak resolution of a peak of a C—H bond of the C1s spectra is performed, and a percentage (peak area ratio) of the separated C—H peak occupying the C1s spectra is calculated. A C—H derived C concentration is calculated by multiplying the calculated C—H peak area ratio by the C concentration.

An arithmetical mean of values obtained by performing the above-mentioned process at different positions of the surface of the magnetic layer of the magnetic recording medium three times is set as the C—H derived C concentration. In addition, the specific aspect of the process described above is shown in examples which will be described later.

As preferred means for adjusting the C—H derived C concentration, a cooling step can be performed in a non-magnetic layer forming step, as will be described later specifically. However, the magnetic recording medium is not limited to a magnetic recording medium manufactured through such a cooling step.

FIB Abrasive Diameter

The FIB abrasive diameter obtained from the secondary ion image obtained by irradiating the surface of the magnetic layer of the magnetic recording medium with the FIB is 0.04 μm to 0.08 μm. It is thought that the FIB abrasive diameter set to be equal to or smaller than 0.08 contributes to the prevention of the chipping of the head element due to the oxide abrasive in the GTT. In addition, it is surmised that the FIB abrasive diameter set to be equal to or greater than 0.04 μm contributes to the removal of a component derived from the magnetic layer attached to the head due to the sliding with the surface of the magnetic layer in the GTT. It is thought that this contributes to prevention of the chipping of the element of the head due to the sliding between the surface of the magnetic layer and the head, in a state where the component derived from the magnetic layer is attached to the head in the GTT. From a viewpoint of further preventing the occurrence of the head element chipping in the GTT, the FIB abrasive diameter is preferably equal to or greater than 0.05 μm and more preferably equal to or greater than 0.06 μm. In addition, from the same viewpoint, the FIB abrasive diameter is preferably equal to or smaller than 0.07 μm. A specific aspect of means for adjusting the FIB abrasive diameter will be described later.

Hereinafter, the magnetic recording medium will be described more specifically.

Magnetic Layer

Ferromagnetic Hexagonal Ferrite Powder

The magnetic layer of the magnetic recording medium includes ferromagnetic hexagonal ferrite powder as ferromagnetic powder. Regarding the ferromagnetic hexagonal ferrite powder, a magnetoplumbite type (also referred to as an “M type”), a W type, a Y type, and a Z type are known as the crystal structure of the hexagonal ferrite. The ferromagnetic hexagonal ferrite powder included in the magnetic layer may have any crystal structure. In addition, an iron atom and a divalent metal atom are included in the crystal structure of the hexagonal ferrite, as constituent atoms. The divalent metal atom is a metal atom which may become divalent cations as ions, and examples thereof include a barium atom, a strontium atom, an alkali earth metal atom such as calcium atom, and a lead atom. For example, the hexagonal ferrite including a barium atom as the divalent metal atom is a barium ferrite, and the hexagonal ferrite including a strontium atom is a strontium ferrite. In addition, the hexagonal ferrite may be a mixed crystal of two or more hexagonal ferrites. As an example of the mixed crystal, a mixed crystal of the barium ferrite and the strontium ferrite can be used.

As an index for a particle size of the ferromagnetic hexagonal ferrite powder, an activation volume can be used. The “activation volume” is a unit of magnetization reversal. Regarding the activation volume described in the invention and the specification, magnetic field sweep rates of a coercivity Hc measurement part at time points of 3 minutes and 30 minutes are measured by using a vibrating sample magnetometer in an environment of an atmosphere temperature 23° C.±1° C., and the activation volume is a value acquired from the following relational expression of Hc and an activation volume V.

Hc=2Ku/Ms{1−[(kT/KuV)ln(At/0.693)]^(1/2)}

[In the expression, Ku: anisotropy constant, Ms: saturation magnetization, k: Boltzmann's constant, T: absolute temperature, V: activation volume, A: spin precession frequency, and t: magnetic field reversal time]

High-density recording is constantly desired in the magnetic recording medium. As a method for achieving high-density recording, a method of decreasing a particle size of ferromagnetic powder included in a magnetic layer and increasing a filling percentage of the ferromagnetic powder of the magnetic layer is used. From this viewpoint, the activation volume of the ferromagnetic hexagonal ferrite powder is preferably equal to or smaller than 2,500 nm³, more preferably equal to or smaller than 2,300 nm³, and even more preferably equal to or smaller than 2,000 nm³. Meanwhile, from a viewpoint of stability of magnetization, the activation volume is, for example, preferably equal to or greater than 800 nm³, more preferably equal to or greater than 1,000 nm³, and even more preferably equal to or greater than 1,200 nm³.

The shape of the particle configuring the ferromagnetic hexagonal ferrite powder is specified by imaging the ferromagnetic hexagonal ferrite powder at a magnification ratio of 100,000 with a transmission electron microscope, and tracing an outline of a particle (primary particle) with a digitizer on a particle image obtained by printing the image on printing paper so that the total magnification of 500,000. The primary particle is an independent particle which is not aggregated. The imaging with a transmission electron microscope is performed by a direct method with a transmission electron microscope at an acceleration voltage of 300 kV. The transmission electron microscope observation and measurement can be, for example, performed with a transmission electron microscope H-9000 manufactured by Hitachi, Ltd. and image analysis software KS-400 manufactured by Carl Zeiss. Regarding the shape of the particle configuring the ferromagnetic hexagonal ferrite powder, a “planar shape” is a shape having two plate surfaces facing each other. Meanwhile, among the shapes of the particles not having such a plate surface, a shape having distinguished long axis and short axis is an “elliptical shape”. The long axis is determined as an axis (linear line) having the longest length of the particle. In contrast, the short axis is determined as an axis having the longest length of the particle in a linear line orthogonal to the long axis. A shape not having distinguished long axis and short axis, that is, a shape in which the length of the long axis is the same as the length of the short axis is a “sphere shape”. From the shapes, a shape in which the long axis and the short axis are hardly specified, is called an undefined shape. The imaging with a transmission electron microscope for specifying the shapes of the particles is performed without performing the alignment process with respect to the imaging target powder. The shape of the ferromagnetic hexagonal ferrite powder used for the preparation of the magnetic layer forming composition and the ferromagnetic hexagonal ferrite powder included in the magnetic layer may be any one of the planar shape, the elliptical shape, the sphere shape, and the undefined shape.

An average particle size of various powders disclosed in the invention and the specification is an arithmetical mean of the values obtained regarding randomly extracted 500 particles by using the particle image which is captured as described above, unless otherwise noted. The average particle size shown in the examples which will be described later is a value obtained by using transmission electron microscope H-9000 manufactured by Hitachi, Ltd. as the transmission electron microscope and image analysis software KS-400 manufactured by Carl Zeiss as the image analysis software.

For details of the ferromagnetic hexagonal ferrite powder, descriptions disclosed in paragraphs 0134 to 0136 of JP2011-216149A can be referred to, for example.

The content (filling percentage) of the ferromagnetic hexagonal ferrite powder of the magnetic layer is preferably 50% to 90% by mass and more preferably 60% to 90% by mass. A high filling percentage of the ferromagnetic hexagonal ferrite powder of the magnetic layer is preferable, from a viewpoint of improving recording density.

Binding Agent and Curing Agent

The magnetic recording medium includes a binding agent in the magnetic layer. The binding agent is one or more kinds of resin. The resin may be a homopolymer or a copolymer. As the binding agent included in the magnetic layer, a resin selected from a polyurethane resin, a polyester resin, a polyamide resin, a vinyl chloride resin, an acrylic resin obtained by copolymerizing styrene, acrylonitrile, or methyl methacrylate, a cellulose resin such as nitrocellulose, an epoxy resin, a phenoxy resin, and a polyvinylalkylal resin such as polyvinyl acetal or polyvinyl butyral can be used alone or a plurality of resins can be mixed with each other to be used. Among these, a polyurethane resin, an acrylic resin, a cellulose resin, and a vinyl chloride resin are preferable. These resins can be used as the binding agent even in the non-magnetic layer and/or a back coating layer which will be described later. For the binding agent described above, description disclosed in paragraphs 0029 to 0031 of JP2010-24113A can be referred to. An average molecular weight of the resin used as the binding agent can be, for example, 10,000 to 200,000 as a weight-average molecular weight. The weight-average molecular weight of the invention and the specification is a value obtained by performing polystyrene conversion of a value measured by gel permeation chromatography (GPC). As the measurement conditions, the following conditions can be used. The weight-average molecular weight shown in examples which will be described later is a value obtained by performing polystyrene conversion of a value measured under the following measurement conditions.

GPC device: HLC-8120 (manufactured by Tosoh Corporation)

Column: TSK gel Multipore HXL-M (manufactured by Tosoh Corporation, 7.8 mmID (inner diameter)×30.0 cm)

Eluent: Tetrahydrofuran (THF)

In addition, a curing agent can also be used together with the resin which can be used as the binding agent, in a case of forming the magnetic layer. As the curing agent, in one aspect, a thermosetting compound which is a compound in which a curing reaction (crosslinking reaction) proceeds due to heating can be used, and in another aspect, a photocurable compound in which a curing reaction (crosslinking reaction) proceeds due to light irradiation can be used. At least a part of the curing agent is included in the magnetic layer in a state of being reacted (crosslinked) with other components such as the binding agent, by proceeding the curing reaction in the manufacturing step of the magnetic recording medium. The preferred curing agent is a thermosetting compound, polyisocyanate is suitable. For details of the polyisocyanate, descriptions disclosed in paragraphs 0124 and 0125 of JP2011-216149A can be referred to, for example. The amount of the curing agent added and used can be, for example, 0 to 80.0 parts by mass with respect to 100.0 parts by mass of the binding agent in the magnetic layer forming composition, and is preferably 50.0 to 80.0 parts by mass, from a viewpoint of improvement of hardness of the magnetic layer.

Fatty Acid and Fatty Acid Amide

The magnetic recording medium includes one or more components selected from the group consisting of fatty acid and fatty acid amide in the magnetic layer side portion on the non-magnetic support. The magnetic layer side portion may include only one or both of fatty acid and fatty acid amide. The inventors have thought that the presence of these components in the extreme outermost surface portion of the magnetic layer by the amount so that the C—H derived C concentration becomes 45 atom % to 65 atom % contributes to prevention of the occurrence of the head element chipping in the GTT.

Examples of fatty acid include lauric acid, myristic acid, palmitic acid, stearic acid, oleic acid, linoleic acid, linolenic acid, behenic acid, erucic acid, and elaidic acid, and stearic acid, myristic acid, and palmitic acid are preferable, and stearic acid is more preferable. Fatty acid may be included in the magnetic layer side portion in a state of salt such as metal salt.

As fatty acid amide, amide of various fatty acid described above, specifically, lauric acid amide, myristic acid amide, palmitic acid amide, and stearic acid amide can be used, for example.

Regarding fatty acid and a derivative of fatty acid (amide and ester which will be described later), a part derived from fatty acid of the fatty acid derivative preferably has a structure which is the same as or similar to that of fatty acid used in combination. As an example, in a case of using stearic acid as the fatty acid, it is preferable to use stearic acid amide and/or stearic acid ester in combination.

In one embodiment, the magnetic recording medium, which contains one or more kinds of components selected from the group consisting of fatty acid and fatty acid amide in the magnetic layer side portion, can be manufactured by forming a magnetic layer with the use of a magnetic layer forming composition which contains one or more kinds of components selected from the group consisting of fatty acid and fatty acid amide. In one embodiment, the magnetic recording medium, which contains one or more kinds of components selected from the group consisting of a fatty acid and a fatty acid amide in the magnetic layer side portion, can be manufactured by forming a non-magnetic layer with the use of a non-magnetic layer forming composition which contains one or more kinds of components selected from the group consisting of fatty acid and fatty acid amide. In one embodiment, the magnetic recording medium, which contains one or more kinds of components selected from the group consisting of fatty acid and fatty acid amide in the magnetic layer side portion, can be manufactured by forming a non-magnetic layer with the use of a non-magnetic layer forming composition which contains one or more kinds of components selected from the group consisting of fatty acid and fatty acid amide, as well as forming a magnetic layer with the use of a magnetic layer forming composition which contains one or more kinds of components selected from the group consisting of fatty acid and fatty acid amide. The non-magnetic layer can play a role of holding a lubricant such as fatty acid or fatty acid amide and supplying the lubricant to the magnetic layer. The lubricant such as fatty acid, fatty acid amide, or the like contained in the non-magnetic layer can move to and be present in the magnetic layer.

The content of fatty acid is, for example, 0.1 to 10.0 parts by mass and is preferably 1.0 to 7.0 parts by mass, with respect to 100.0 parts by mass of the ferromagnetic hexagonal ferrite powder, as the content in the magnetic layer forming composition. In a case where two or more different fatty acids are added to the magnetic layer forming composition, the content thereof is a total content of the two or more different fatty acids. This point applies to contents of other components, in the same manner. In addition, in the invention and the specification, a given component may be used alone or used in combination of two or more kinds thereof, unless otherwise noted.

The content of fatty acid amide in the magnetic layer forming composition is, for example, 0.1 to 3.0 parts by mass and is preferably 0.1 to 1.0 part by mass with respect to 100.0 parts by mass of ferromagnetic hexagonal ferrite powder.

Meanwhile, the content of fatty acid in the non-magnetic layer forming composition is, for example, 1.0 to 10.0 parts by mass and is preferably 1.0 to 7.0 parts by mass with respect to 100.0 parts by mass of non-magnetic powder. In addition, the content of fatty acid amide in the non-magnetic layer forming composition is, for example, 0.1 to 3.0 parts by mass and is preferably 0.1 to 1.0 parts by mass with respect to 100.0 parts by mass of non-magnetic powder.

Oxide Abrasive

The magnetic recording medium includes an oxide abrasive in the magnetic layer. The oxide abrasive is a non-magnetic oxide powder having Mohs hardness exceeding 8 and is preferably a non-magnetic oxide powder having Mohs hardness equal to or greater than 9. A maximum value of Mohs hardness is 10. The oxide abrasive may be an inorganic oxide powder and an organic oxide powder, and is preferably an inorganic oxide powder. Specifically, examples of the abrasive include powders of alumina (Al₂O₃), titanium oxide (TiO₂), cerium oxide (CeO₂), and zirconium oxide (ZrO₂), and alumina powder is preferable among these. Mohs hardness of alumina is approximately 9. For alumina powder, a description disclosed in a paragraph 0021 of JP2013-229090A can also be referred to. In addition, as an index of a particle size of the oxide abrasive, a specific surface area can be used. It is thought that, as the specific surface area is great, the particle size of the primary particles of the particles configuring the oxide abrasive is small. As the oxide abrasive, an oxide abrasive in which a specific surface area measured by a Brunauer-Emmett-Teller (BET) method (hereinafter, referred to as a “BET specific surface area”) is equal to or greater than 14 m²/g, is preferably used. In addition, from a viewpoint of dispersibility, an oxide abrasive having a BET specific surface area equal to or smaller than 40 m²/g is preferably used. The content of the oxide abrasive in the magnetic layer is preferably 1.0 to 20.0 parts by mass and more preferably 1.0 to 10.0 parts by mass with respect to 100.0 parts by mass of the ferromagnetic hexagonal ferrite powder.

Additives

The magnetic layer may further include one or more kinds of additives, if necessary. As the additives, the curing agent described above is used as an example. In addition, examples of the additive which can be included in the magnetic layer include a non-magnetic powder other than the oxide abrasive, a lubricant, a dispersing agent, a dispersing assistant, an antibacterial agent, an antistatic agent, and an antioxidant. As the additives, a commercially available product can be suitably selected or manufactured by a well-known method according to the desired properties, and any amount thereof can be used. For example, for the dispersing agent, a description disclosed in paragraphs 0061 and 0071 of JP2012-133837A can be referred to. The dispersing agent may be included in the non-magnetic layer. For the dispersing agent which can be included in the non-magnetic layer, a description disclosed in a paragraph 0061 of JP2012-133837A can be referred to.

In addition, as the dispersing agent, a dispersing agent for increasing dispersibility of the oxide abrasive can be used. As a compound which can function as such a dispersing agent, an aromatic hydrocarbon compound including a phenolic hydroxyl group can be used. The “phenolic hydroxyl group” is a hydroxyl group directly bonded to an aromatic ring. The aromatic ring included in the aromatic hydrocarbon compound may be a monocycle, may have a polycyclic structure, or may be a condensed ring. From a viewpoint of improving dispersibility of the abrasive, an aromatic hydrocarbon compound including a benzene ring or a naphthalene ring is preferable. In addition, the aromatic hydrocarbon compound may include a substituent other than the phenolic hydroxyl group. Examples of the substituent other than the phenolic hydroxyl group include a halogen atom, an alkyl group, an alkoxy group, an amino group, an acyl group, a nitro group, a nitroso group, and a hydroxyalkyl group, and a halogen atom, an alkyl group, an alkoxy group, an amino group, and a hydroxyalkyl group are preferable. The number of phenolic hydroxyl groups included in one molecule of the aromatic hydrocarbon compound may be one, two, three, or greater.

As a preferable aspect of the aromatic hydrocarbon compound including the phenolic hydroxyl group, a compound represented by General Formula 100 can be used.

[In General Formula 100, two of X¹⁰¹ to X¹⁰⁸ are hydroxyl groups and the other six thereof each independently represent a hydrogen atom or a substituent.]

In the compound represented by General Formula 100, substituent positions of the two hydroxyl groups (phenolic hydroxyl groups) are not particularly limited.

In the compound represented by General Formula 100, two of X¹⁰¹ to X¹⁰⁸ are hydroxyl groups (phenolic hydroxyl groups) and the other six thereof each independently represent a hydrogen atom or a substituent. In addition, among X¹⁰¹ to X¹⁰⁸, all of the part other than the two hydroxyl groups may be a hydrogen atom or a part or all thereof may be a substituent. As the substituent, the substituent described above can be used. As the substituent other than the two hydroxyl groups, one or more phenolic hydroxyl groups may be included. From a viewpoint of improving dispersibility of the abrasive, it is preferable that the substituent other than the two hydroxyl groups of X¹⁰¹ to X¹⁰⁸ is not a phenolic hydroxyl group. That is, the compound represented by General Formula 100 is preferably dihydroxynaphthalene or a derivative thereof, and more preferably 2,3-dihydroxynaphthalene or a derivative thereof. Examples of the preferable substituent represented by X¹⁰¹ to X¹⁰⁸ include a halogen atom (for example, a chlorine atom or a bromine atom), an amino group, an alkyl group having 1 to 6 (preferably 1 to 4) carbon atoms, a methoxy group, an ethoxy group, an acyl group, a nitro group, a nitroso group, and a —CH₂OH group.

In addition, for the dispersing agent for increasing dispersibility of the oxide abrasive, a description disclosed in paragraphs 0024 to 0028 of JP2014-179149A can be referred to.

The used amount of the dispersing agent for increasing dispersibility of the oxide abrasive can be, for example, 0.5 to 20.0 parts by mass and is preferably 1.0 to 10.0 parts by mass with respect to 100.0 parts by mass of the abrasive in a case of preparing a magnetic layer forming composition (preferably, in a case of preparing an abrasive solution as will be described later).

As the dispersing agent, a well-known dispersing agent for increasing dispersibility of ferromagnetic hexagonal ferrite powder such as a carboxyl group-containing compound or a nitrogen-containing compound can also be used. For example, the nitrogen-containing compound may primary amine represented by NH₂R, secondary amine represented by NHR₂, or tertiary amine represented by NR₃. As described above, R indicates any structure configuring the nitrogen-containing compound and a plurality of R may be the same as each other or different from each other. The nitrogen-containing compound may be a compound (polymer) having a plurality of repeating structures in a molecule. It is thought that a nitrogen-containing portion of the nitrogen-containing compound functioning as an adsorption portion to the surface of the particles of the ferromagnetic hexagonal ferrite powder is a reason for the nitrogen-containing compound to function as the dispersing agent. As the carboxyl group-containing compound, for example, fatty acid of oleic acid can be used. Regarding the carboxyl group-containing compound, it is thought that a carboxyl group functioning as an adsorption portion to the surface of the particles of the ferromagnetic hexagonal ferrite powder is a reason for the carboxyl group-containing compound to function as the dispersing agent. It is also preferable to use the carboxyl group-containing compound and the nitrogen-containing compound in combination. The amount of these dispersing agents used can be suitably set.

As the non-magnetic powder other than the oxide abrasive included in the magnetic layer, non-magnetic powder which can contribute to formation of projections on the surface of the magnetic layer to control of friction properties (hereinafter, also referred to as a “projection formation agent”). As the projection formation agent, various non-magnetic powders generally used as the projection formation agent in the magnetic layer can be used. These may be powder of inorganic substance (inorganic powder) or powder of organic substance (organic powder). In one aspect, from a viewpoint of homogenization of friction properties, particle size distribution of the projection formation agent is not polydispersion having a plurality of peaks in the distribution and is preferably monodisperse showing a single peak. From a viewpoint of availability of monodisperse particles, the projection formation agent is preferably inorganic powder. Examples of the inorganic powder include powder of metal oxide, metal carbonate, metal sulfate, metal nitride, metal carbide, and metal sulfide. The particles configuring the projection formation agent (non-magnetic powder other than the oxide abrasive) are preferably colloid particles and more preferably inorganic oxide colloid particles. In addition, from a viewpoint of availability of monodisperse particles, the inorganic oxide configuring the inorganic oxide colloid particles are preferably silicon dioxide (silica). The inorganic oxide colloid particles are more preferably colloidal silica (silica colloid particles). In the invention and the specification, the “colloid particles” are particles which are not precipitated and dispersed to generate a colloidal dispersion, in a case where 1 g of the particles is added to 100 mL of at least one organic solvent of methyl ethyl ketone, cyclohexanone, toluene, or ethyl acetate, or a mixed solvent including two or more kinds of the solvent described above at a random mixing ratio. In another aspect, the projection formation agent is preferably carbon black. An average particle size of the projection formation agent can be, for example, 30 to 300 nm and is preferably 40 to 200 nm. In addition, from a viewpoint that the projection formation agent exhibits the functions thereof in more excellent manner, the content of the projection formation agent in the magnetic layer is preferably 1.0 to 4.0 parts by mass and more preferably 1.5 to 3.5 parts by mass with respect to 100.0 parts by mass of the ferromagnetic hexagonal ferrite powder.

In addition, one or both of the magnetic layer and the non-magnetic layer which will be described later in detail may or may not include fatty acid ester.

All of fatty acid ester, fatty acid, and fatty acid amide are components which can function as a lubricant. The lubricant is generally broadly divided into a fluid lubricant and a boundary lubricant. Fatty acid ester is called a component which can function as a fluid lubricant, whereas fatty acid and fatty acid amide is called as a component which can function as a boundary lubricant. It is considered that the boundary lubricant is a lubricant which can be adsorbed to a surface of powder (for example, ferromagnetic powder) and form a rigid lubricant film to decrease contact friction. Meanwhile, it is considered that the fluid lubricant is a lubricant which can form a liquid film on a surface of a magnetic layer to decrease flowing of the liquid film. As described above, it is considered that the operation of fatty acid ester is different from the operation fatty acid and fatty acid amide as the lubricants. The inventors have surmised that the setting of the C—H derived C concentration which is considered as an index for the presence amount of one or more components selected from the group consisting of fatty acid and fatty acid amide in the extreme outermost surface portion of the magnetic layer to be 45 atom % to 65 atom % contributes to prevention of the occurrence of the head element chipping in the GTT.

As fatty acid ester, esters of various fatty acids described above regarding fatty acid can be used. Specific examples thereof include butyl myristate, butyl palmitate, butyl stearate (butyl stearate), neopentyl glycol dioleate, sorbitan monostearate, sorbitan distearate, sorbitan tristearate, oleyl oleate, isocetyl stearate, isotridecyl stearate, octyl stearate, isooctyl stearate, amyl stearate, and butoxyethyl stearate.

The content of fatty acid ester of the magnetic layer forming composition is, for example, 0 to 10.0 parts by mass and is preferably 1.0 to 7.0 parts by mass with respect to 100.0 parts by mass of ferromagnetic hexagonal ferrite powder.

In addition, the content of fatty acid ester in the non-magnetic layer forming composition is, for example, 0 to 10.0 parts by mass and is preferably 1.0 to 7.0 parts by mass with respect to 100.0 parts by mass of non-magnetic powder.

The magnetic layer described above can be provided on the surface of the non-magnetic support directly or indirectly through the non-magnetic layer.

Non-Magnetic Layer

Next, the non-magnetic layer will be described.

The magnetic recording medium may include a magnetic layer directly on a surface of a non-magnetic support, or may include a non-magnetic layer including a non-magnetic powder and a binding agent between the non-magnetic support and the magnetic layer. The non-magnetic powder included in the non-magnetic layer may be inorganic powder or organic powder. In addition, carbon black and the like can be used. Examples of the inorganic powder include powder of metal, metal oxide, metal carbonate, metal sulfate, metal nitride, metal carbide, and metal sulfide. These non-magnetic powder can be purchased as a commercially available product or can be manufactured by a well-known method. For details thereof, descriptions disclosed in paragraphs 0036 to 0039 of JP2010-24113A can be referred to. A content (filling percentage) of the non-magnetic powder in the non-magnetic layer is preferably 50% to 90% by mass and more preferably 60% to 90% by mass.

In regards to other details of a binding agent or additives of the non-magnetic layer, the well-known technology regarding the non-magnetic layer can be applied. In addition, in regards to the type and the content of the binding agent, and the type and the content of the additive, for example, the well-known technology regarding the magnetic layer can be applied.

In the invention and the specification, the non-magnetic layer also includes a substantially non-magnetic layer including a small amount of ferromagnetic powder as impurities or intentionally, together with the non-magnetic powder. Here, the substantially non-magnetic layer is a layer having a residual magnetic flux density equal to or smaller than 10 mT, a layer having coercivity equal to or smaller than 7.96 kA/m(100 Oe), or a layer having a residual magnetic flux density equal to or smaller than 10 mT and coercivity equal to or smaller than 7.96 kA/m(100 Oe). It is preferable that the non-magnetic layer does not have a residual magnetic flux density and coercivity.

Non-Magnetic Support

Next, the non-magnetic support (hereinafter, also simply referred to as a “support”) will be described.

As the non-magnetic support, well-known components such as polyethylene terephthalate, polyethylene naphthalate, polyamide, polyamide imide, aromatic polyamide subjected to biaxial stretching are used. Among these, polyethylene terephthalate, polyethylene naphthalate, and polyamide are preferable. Corona discharge, plasma treatment, easy-bonding treatment, or heat treatment may be performed with respect to these supports in advance.

Back Coating Layer

The magnetic recording medium can also include a back coating layer including non-magnetic powder and a binding agent on a surface side of the non-magnetic support opposite to the surface side provided with the magnetic layer. The back coating layer preferably includes any one or both of carbon black and inorganic powder. For the binding agent included in the back coating layer and various additives which can be randomly included therein, a well-known technology regarding the back coating layer can be applied, and a well-known technology regarding the process of the magnetic layer and/or the non-magnetic layer can also be applied. For example, for the back coating layer, descriptions disclosed in paragraphs 0018 to 0020 of JP2006-331625A and page 4, line 65, to page 5, line 38, of U.S. Pat. No. 7,029,774 can be referred to.

Various Thicknesses

Thicknesses of the non-magnetic support and each layer of the magnetic recording medium will be described below.

A thickness of the non-magnetic support is, for example, 3.0 to 80.0 μm, preferably 3.0 to 50.0 μm, and more preferably 3.0 to 10.0 μm.

A thickness of the magnetic layer can be optimized according to a saturation magnetization amount of a magnetic head used, a head gap length, a recording signal band, and the like. The thickness of the magnetic layer is generally 10 nm to 100 nm, preferably 20 to 90 nm, and more preferably 30 to 70 nm, from a viewpoint of realization of high-density recording. The magnetic layer may be at least one layer, or the magnetic layer can be separated to two or more layers having different magnetic properties, and a configuration regarding a well-known multilayered magnetic layer can be applied. A thickness of the magnetic layer which is separated into two or more layers is a total thickness of the layers.

A thickness of the non-magnetic layer is, for example, equal to or greater than 50 nm, preferably equal to or greater than 70 nm, and more preferably equal to or greater than 100 nm. Meanwhile, the thickness of the non-magnetic layer is preferably equal to or smaller than 800 nm and more preferably equal to or smaller than 500 nm.

A thickness of the back coating layer is preferably equal to or smaller than 0.9 μm and more preferably 0.1 to 0.7 μm.

The thicknesses of various layers of the magnetic recording medium and the non-magnetic support can be acquired by a well-known film thickness measurement method. As an example, a cross section of the magnetic recording medium in a thickness direction is, for example, exposed by a well-known method of ion beams or microtome, and the exposed cross section is observed with an electron microscope such as a scanning electron microscope or a transmission electron microscope. In the cross section observation, various thicknesses can be acquired as a thickness acquired at one portion of the cross section in the thickness direction, or an arithmetical mean of thicknesses acquired at a plurality of portions of two or more portions, for example, two portions which are randomly extracted. In addition, the thickness of each layer may be acquired as a designed thickness calculated according to the manufacturing conditions.

Manufacturing Step

Preparation of Each Layer Forming Composition

Steps of preparing the composition for forming the magnetic layer, the non-magnetic layer, or the back coating layer generally include at least a kneading step, a dispersing step, and a mixing step provided before and after these steps, if necessary. Each step may be divided into two or more stages. The components used in the preparation of each layer forming composition may be added at an initial stage or in a middle stage of each step. As the solvent, one kind or two or more kinds of various solvents generally used for manufacturing a coating type magnetic recording medium can be used. For the solvent, a description disclosed in a paragraph 0153 of JP2011-216149A can be referred to, for example. In addition, each component may be separately added in two or more steps. For example, the binding agent may be separately added in the kneading step, the dispersing step, and a mixing step for adjusting a viscosity after the dispersion. In order to manufacture the magnetic recording medium, a well-known manufacturing technology of the related art can be used in various steps. In the kneading step, an open kneader, a continuous kneader, a pressure kneader, or a kneader having a strong kneading force such as an extruder is preferably used. For details of these kneading processes, descriptions disclosed in JP1989-106338A (JP-H01-106338A) and JP1989-79274A (JP-H01-79274A) can be referred to. As a disperser, a well-known disperser can be used. The filtering may be performed by a well-known method in any stage for preparing each layer forming composition. The filtering can be performed by using a filter, for example. As the filter used in the filtering, a filter having a hole diameter of 0.01 to 3 μm (for example, filter made of glass fiber or filter made of polypropylene) can be used, for example.

The value of the FIB abrasive diameter tends to decrease, as the oxide abrasive is present in a finer state in the magnetic layer. As a means for causing the oxide abrasive to be present in a finer state in the magnetic layer, a dispersing agent capable of increasing dispersibility of the oxide abrasive can be used, as described above. In addition, in order to cause the oxide abrasive to be present in a finer state in the magnetic layer, it is preferable that an abrasive having a small particle size is used, aggregation of the abrasive is prevented, and uneven distribution is prevented to disperse the abrasive in the magnetic layer evenly. As a means for this, a method of reinforcing dispersion conditions of the oxide abrasive in a case of preparing the magnetic layer forming composition is used. For example, dispersing the oxide abrasive separately from the ferromagnetic hexagonal ferrite powder is one aspect of the reinforcement of the dispersion conditions. The separate dispersion is specifically a method of preparing a magnetic layer forming composition through a step of mixing an abrasive solution including an oxide abrasive and a solvent (here, ferromagnetic hexagonal ferrite powder is not substantially included) with a magnetic liquid including the ferromagnetic hexagonal ferrite powder, a solvent, and a binding agent. By performing the mixing after dispersing the oxide abrasive separately from the ferromagnetic hexagonal ferrite powder, it is possible to increase dispersibility of the oxide abrasive in the magnetic layer forming composition. The expression “ferromagnetic hexagonal ferrite powder is not substantially included” means that the ferromagnetic hexagonal ferrite powder is not added as a constituent element of the abrasive solution, and a small amount of the ferromagnetic hexagonal ferrite powder mixed as impurities without any intention is allowed. In addition to the separate dispersion or with the separate dispersion, means such as the dispersion process performed for a long period of time, the use of dispersion medium having a small size (for example, a decrease in diameter of dispersion beads in the beads dispersion), a high degree of filling of the dispersion medium in the disperser can be randomly combined to reinforce the dispersion conditions. For the disperser and the dispersion medium, a commercially available product can be used. In addition, a centrifugal separation process of the abrasive solution contributes to the oxide abrasive present in the magnetic layer in a finer state, by removing particles having a size greater than an average particle size and/or aggregated particles from the particles configuring the oxide abrasive. The centrifugal separation process can be performed by a commercially available centrifugal separator. In addition, the filtering of the abrasive solution performed by using a filter or the like is preferable for removing a coarse aggregate of the aggregated particles configuring the oxide abrasive. The removal of such coarse aggregate can contribute to the oxide abrasive present in the magnetic layer in a finer state. For example, the filtering by using a filter having a smaller hole diameter can contribute to the oxide abrasive present in the magnetic layer in a finer state. In addition, by adjusting various process conditions (for example, stirring conditions, dispersion process conditions, filtering conditions, and the like) after mixing the oxide solution with the component for preparing the magnetic layer forming composition such as the ferromagnetic hexagonal ferrite powder or the like, it is possible to increase dispersibility of the oxide abrasive in the magnetic layer forming composition. This can also contribute to the oxide abrasive present in the magnetic layer in a finer state. However, in a case where the oxide abrasive is present in the magnetic layer in an extremely finer state, the FIB abrasive diameter may be smaller than 0.04 μm, and therefore, it is preferable that various conditions for preparing the abrasive solution are adjusted so as to realize the FIB abrasive diameter of 0.04 μm to 0.08 μm.

Regarding the dispersion process of the magnetic layer forming composition, as described above, it is preferable to prevent the occurrence of chipping. In order for this, it is preferable to perform the dispersion process of the ferromagnetic hexagonal ferrite powder by a dispersion process having two stages, in which a coarse aggregate of the ferromagnetic hexagonal ferrite powder is crushed by the dispersion process in a first stage, and the dispersion process in a second stage, in which a collision energy applied to particles of the ferromagnetic hexagonal ferrite powder due to collision with the dispersion beads is smaller than that in the first dispersion process, is performed, in the step of preparing the magnetic layer forming composition. According to such a dispersion process, it is possible to improve dispersibility of the ferromagnetic hexagonal ferrite powder and prevent the occurrence of chipping.

As a preferred aspect of the dispersion process having two stages, a dispersion process including a first stage of obtaining a dispersion liquid by performing the dispersion process of the ferromagnetic hexagonal ferrite powder, the binding agent, and the solvent under the presence of first dispersion beads, and a second stage of performing the dispersion process of the dispersion liquid obtained in the first stage under the presence of second dispersion beads having smaller bead diameter and density than those of the first dispersion beads can be used. Hereinafter, the dispersion process of the preferred aspect described above will be further described.

In order to increase the dispersibility of the ferromagnetic hexagonal ferrite powder, the first stage and the second stage are preferably performed as the dispersion process before mixing the ferromagnetic hexagonal ferrite powder and other powder components. For example, the first stage and the second stage are preferably performed as a dispersion process of a solution (magnetic liquid) including ferromagnetic hexagonal ferrite powder, a binding agent, a solvent, and randomly added additives, before mixing the oxide abrasive (preferably before mixing the oxide abrasive and the projection formation agent described above).

A bead diameter of the second dispersion bead is preferably equal to or smaller than 1/100 and more preferably equal to or smaller than 1/500 of a bead diameter of the first dispersion bead. The bead diameter of the second dispersion bead can be, for example, equal to or greater than 1/10,000 of the bead diameter of the first dispersion bead. However, there is no limitation to this range. The bead diameter of the second dispersion bead is, for example, preferably 80 to 1,000 nm. Meanwhile, the bead diameter of the first dispersion bead can be, for example, 0.2 to 1.0 mm.

The bead diameter of the invention and the specification is a value measured by the same method as the measurement method of the average particle size of the powder described above.

The second stage is preferably performed under the conditions in which the amount of the second dispersion beads is equal to or greater than 10 times of the amount of the ferromagnetic hexagonal ferrite powder, and is more preferably performed under the conditions in which the amount of the second dispersion beads is 10 times to 30 times of the amount of the ferromagnetic hexagonal ferrite powder, based on mass.

Meanwhile, the amount of the dispersion beads in the first stage is preferably in the range described above.

The second dispersion beads are beads having lower density than that of the first dispersion beads. The “density” is obtained by dividing the mass (unit: g) of the dispersion beads by volume (unit: cm³). The measurement is performed by the Archimedes method. The density of the second dispersion beads is preferably equal to or lower than 3.7 g/cm³ and more preferably equal to or lower than 3.5 g/cm³. The density of the second dispersion beads may be, for example, equal to or higher than 2.0 g/cm³ or may be lower than 2.0 g/cm³. As the preferred second dispersion beads from a viewpoint of density, diamond beads, silicon carbide beads, or silicon nitride beads can be used, and as preferred second dispersion beads from a viewpoint of density and hardness, diamond beads can be used.

Meanwhile, as the first dispersion beads, dispersion beads having density exceeding 3.7 g/cm³ are preferable, dispersion beads having density equal to or higher than 3.8 g/cm³ are more preferable, and dispersion beads having density equal to or higher than 4.0 g/cm³ are even more preferable. The density of the first dispersion beads may be, for example, equal to or smaller than 7.0 g/cm³ or may exceed 7.0 g/cm³. As the first dispersion beads, zirconia beads or alumina beads are preferably used, and zirconia beads are more preferably used.

The dispersion time is not particularly limited and may be set in accordance with the kind of a disperser used.

Coating Step, Cooling Step, Heating and Drying Step

The magnetic layer can be formed by directly applying the magnetic layer forming composition onto the non-magnetic support or performing multilayer coating of the magnetic layer forming composition with the non-magnetic layer forming composition in order or at the same time. For details of the coating for forming each layer, a description disclosed in a paragraph 0066 of JP2010-231843A can be referred to.

As described above, in one aspect, the magnetic recording medium includes the non-magnetic layer between the non-magnetic support and the magnetic layer. Such a magnetic recording medium can be preferably manufactured by successive multilayer coating. A manufacturing step of performing the successive multilayer coating can be preferably performed as follows. The non-magnetic layer is formed through a coating step of applying a non-magnetic layer forming composition onto a non-magnetic support to form a coating layer, and a heating and drying step of drying the formed coating layer by a heating process. In addition, the magnetic layer is formed through a coating step of applying a magnetic layer forming composition onto the formed non-magnetic layer to form a coating layer, and a heating and drying step of drying the formed coating layer by a heating process.

In the non-magnetic layer forming step of the manufacturing method of performing such successive multilayer coating, it is preferable to perform a coating step by using the non-magnetic layer forming composition including one or more components selected from the group consisting of fatty acid and fatty acid amide and to perform a cooling step of cooling the coating layer between the coating step and the heating and drying step, in order to adjust the C—H derived C concentration to be 45 atom % to 65 atom % in the magnetic recording medium including at least one or more components selected from the group consisting of fatty acid and fatty acid amide in the magnetic layer. The reason thereof is not clear, but it is surmised that the reason thereof is because the components (fatty acid and/or fatty acid amide) are moved to the surface of the non-magnetic layer at the time of solvent volatilization of the heating and drying step, by cooling the coating layer of the non-magnetic layer forming composition before the heating and drying step. However, this is merely the surmise, and the invention is not limited thereto.

In the magnetic layer forming step, a coating step of applying a magnetic layer forming composition including a ferromagnetic hexagonal ferrite powder, a binding agent, an oxide abrasive, a component selected from the group consisting of fatty acid and fatty acid amide, and a solvent onto a non-magnetic layer to form a coating layer, and a heating and drying step of drying the formed coating layer by a heating process can be performed.

Hereinafter, a specific aspect of the manufacturing method of the magnetic recording medium tape will be described with reference to FIG. 1. However, the invention is not limited to the following specific aspect.

FIG. 1 is a step schematic view showing a specific aspect of a step of manufacturing the magnetic recording medium including a non-magnetic layer and a magnetic layer in this order on one surface of a non-magnetic support and including a back coating layer on the other surface thereof. In the aspect shown in FIG. 1, an operation of sending a non-magnetic support (elongated film) from a sending part and winding the non-magnetic support around a winding part is continuously performed, and various processes of coating, drying, and alignment are performed in each part or each zone shown in FIG. 1, and thus, it is possible to sequentially form a non-magnetic layer and a magnetic layer on one surface of the running non-magnetic support by multilayer coating and to form a back coating layer on the other surface thereof. In the aspect shown in FIG. 1, the manufacturing step which is normally performed for manufacturing the coating type magnetic recording medium can be performed in the same manner except for including a cooling zone.

The non-magnetic layer forming composition is applied onto the non-magnetic support sent from the sending part in a first coating part (coating step of non-magnetic layer forming composition).

After the coating step, a coating layer of the non-magnetic layer forming composition formed in the coating step is cooled in a cooling zone (cooling step). For example, it is possible to perform the cooling step by allowing the non-magnetic support on which the coating layer is formed to pass through a cooling atmosphere. An atmosphere temperature of the cooling atmosphere is preferably −10° C. to 0° C. and more preferably −5° C. to 0° C. The time for performing the cooling step (for example, time while any part of the coating layer is delivered to and sent from the cooling zone (hereinafter, also referred to as a “staying time”)) is not particularly limited, and in a case where the time described above is long, the C—H derived C concentration tends to be increased. Thus, the time described above is preferably adjusted by performing preliminary experiment if necessary, so that the C—H derived C concentration of 45 atom % to 65 atom % is realized. In the cooling step, cooled air may blow to the surface of the coating layer.

After the cooling zone, in a first heating process zone, the coating layer is heated after the cooling step to dry the coating layer (heating and drying step). The heating and drying process can be performed by causing the non-magnetic support including the coating layer after the cooling step to pass through the heated atmosphere. An atmosphere temperature of the heated atmosphere here is, for example, approximately 60° to 140°. Here, the atmosphere temperature may be a temperature at which the solvent is volatilized and the coating layer is dried, and the atmosphere temperature is not limited to the atmosphere temperature in the range described above. In addition, the heated air may blow to the surface of the coating layer. The points described above are also applied to a heating and drying step of a second heating process zone and a heating and drying step of a third heating process zone which will be described later, in the same manner.

Next, in a second coating part, the magnetic layer forming composition is applied onto the non-magnetic layer formed by performing the heating and drying step in the first heating process zone (coating step of magnetic layer forming composition).

After that, in the aspect of performing the alignment process, while the coating layer of the magnetic layer forming composition is wet, an alignment process of the ferromagnetic hexagonal ferrite powder in the coating layer is performed in an alignment zone. For the alignment process, various well-known technologies such as a description disclosed in a paragraph 0067 of JP2010-231843A can be used. As described above, it is preferable to perform the homeotropic alignment process as the alignment process, from a viewpoint of controlling the XRD intensity ratio. Regarding the alignment process, the above description can also be referred to.

The coating layer after the alignment process is subjected to the heating and drying step in the second heating process zone.

Next, in the third coating part, a back coating layer forming composition is applied to a surface of the non-magnetic support on a side opposite to the surface where the non-magnetic layer and the magnetic layer are formed, to form a coating layer (coating step of back coating layer forming composition). After that, the coating layer is heated and dried in the third heating process zone.

By the step described above, it is possible to obtain the magnetic recording medium including the non-magnetic layer and the magnetic layer in this order on one surface of the non-magnetic support and including the back coating layer on the other surface thereof.

In order to manufacture the magnetic recording medium, well-known various processes for manufacturing the coating type magnetic recording medium can be performed. For example, for various processes, descriptions disclosed in paragraphs 0067 to 0069 of JP2010-231843A can be referred to.

As described above, it is possible to obtain the magnetic recording medium according to one aspect of the invention. However, the manufacturing method described above is merely an example, values of the XRD intensity ratio, the vertical squareness ratio, the C—H derived C concentration of the magnetic layer, and the FIB abrasive diameter can be controlled to be in respective ranges described above by any means capable of adjusting the values thereof, and such an aspect is also included in the invention.

The magnetic recording medium according to one aspect of the invention can be a tape-shaped magnetic recording medium (magnetic tape) or can also be a disk-shaped magnetic recording medium (magnetic disk). For example, the magnetic tape is normally accommodated in a magnetic tape cartridge and the magnetic tape cartridge is mounted in a magnetic recording and reproducing device. A servo pattern can also be formed in the magnetic tape by a well-known method, in order to allow head tracking servo to be performed in the magnetic recording and reproducing device.

Magnetic Recording and Reproducing Device

One aspect of the invention relates to a magnetic recording and reproducing device including the magnetic recording medium and a magnetic head.

In the invention and the specification, the “magnetic recording and reproducing device” means a device capable of performing at least one of the recording of information on the magnetic recording medium or the reproducing of information recorded on the magnetic recording medium. Such a device is generally called a drive. The magnetic head included in the magnetic recording and reproducing device can be a recording head capable of performing the recording of information on the magnetic recording medium, or can be a reproducing head capable of performing the reproducing of information recorded on the magnetic recording medium. In addition, in one aspect, the magnetic recording and reproducing device can include both of a recording head and a reproducing head as separate magnetic heads. In another aspect, the magnetic head included in the magnetic recording and reproducing device can also have a configuration of including both of a recording element and a reproducing element in one magnetic head. In addition, the magnetic head which performs the recording of information and/or the reproducing of information may include a servo pattern reading element. Alternatively, as a head other than the magnetic head which performs the recording of information and/or the reproducing of information, a magnetic head (servo head) including a servo pattern reading element may be included in the magnetic recording and reproducing device.

In the magnetic recording and reproducing device, the recording of information on the magnetic recording medium and the reproducing of information recorded on the magnetic recording medium can be performed by bringing the surface of the magnetic layer of the magnetic recording medium into contact with the magnetic head and sliding. The magnetic recording and reproducing device may include the magnetic recording medium according to one aspect of the invention and well-known technologies can be applied for other configurations.

The magnetic recording medium according to one aspect of the invention can exhibit excellent electromagnetic conversion characteristics in the magnetic recording and reproducing device. That is, in the magnetic recording and reproducing device, the information recorded on the magnetic recording medium according to one aspect of the invention can be reproduced at a high SNR. In addition, in the magnetic recording and reproducing device, the GTT can be performed while changing the magnetic recording medium with a new product. In this GTT, according to the magnetic recording medium according to one aspect of the invention, it is possible to prevent occurrence of the head element chipping. The element for preventing the occurrence of the head element chipping can be one or more elements selected from the group consisting of a reproducing element, recording element, and a servo pattern reading element, and two or more elements can also be used. The reproducing element is preferably a magnetoresistive (MR) element capable of reading information recorded on the magnetic recording medium with excellent sensitivity. In addition, the MR element is also preferable as the servo pattern reading element. As a head (MR head) including the MR element as the reproducing element and/or the servo pattern reading element, various well-known MR heads can be used.

EXAMPLES

Hereinafter, the invention will be described with reference to examples. However, the invention is not limited to aspects shown in the examples. “Parts” and “%” in the following description mean “parts by mass” and “% by mass”, unless otherwise noted. In addition, steps and evaluations described below are performed in an environment of an atmosphere temperature of 23° C.±1° C., unless otherwise noted. Further, “eq” described below is an equivalent which is a unit which cannot be converted into the SI unit system.

Example 1

A list of each layer forming composition is shown below.

Preparation of Abrasive Solution

The amount of 2,3-dihydroxynaphthalene (manufactured by Tokyo Chemical Industry Co., Ltd.) shown in condition C of Table 5, 31.3 parts of a 32% solution (solvent is a mixed solvent of methyl ethyl ketone and toluene) of a polyester polyurethane resin having a SO₃Na group as a polar group (UR-4800 (amount of a polar group: 80 meq/kg) manufactured by Toyobo Co., Ltd.), and 570.0 parts of a mixed solution of methyl ethyl ketone and cyclohexanone (mass ratio of 1:1) as a solvent were mixed in 100.0 parts of an oxide abrasive (alumina powder) shown in condition C of Table 5, and dispersed in the presence of zirconia beads (bead diameter: 0.1 mm) by a paint shaker for 5 a period of time shown in condition C of Table 5 (bead dispersion time). After the dispersion, the centrifugal separation process of a dispersion liquid obtained by separating the dispersion liquid from the beads by mesh was performed. The centrifugal separation process was performed by using CS150GXL manufactured by Hitachi, Ltd. (rotor used is S 100AT6 manufactured by Hitachi, Ltd.) as a centrifugal separator at a rotation per minute (rpm) shown in the condition C of Table 5, for a period of time (centrifugal separation time) shown in the condition C of Table 5. After that, the filtering was performed by using a filter having a hole diameter shown in the condition C of Table 5, and an alumina dispersion (abrasive solution) was obtained.

Preparation of Magnetic Layer Forming Composition

Magnetic Liquid

Plate-shaped ferromagnetic hexagonal ferrite powder (M-type barium ferrite): 100.0 parts

-   -   (Activation volume: 1,500 nm³)

Oleic acid: 2.0 parts

A vinyl chloride copolymer (MR-104 manufactured by Zeon Corporation): 10.0 parts

SO₃Na group-containing polyurethane resin: 4.0 parts

-   -   (Weight-average molecular weight: 70,000, SO₃Na group: 0.07         meq/g)

An amine-based polymer (DISPERBYK-102 manufactured by BYK Additives & Instruments): 6.0 parts

Methyl ethyl ketone: 150.0 parts

Cyclohexanone: 150.0 parts

Abrasive Solution

Abrasive solution described above: 6.0 parts

Projection Formation Agent Liquid (Silica Sol)

Colloidal silica: 2.0 parts

-   -   (Average particle size: 80 nm)

Methyl ethyl ketone: 8.0 parts

Other components

Stearic acid: 3.0 parts

Stearic acid amide: 0.3 parts

Butyl stearate: 6.0 parts

Methyl ethyl ketone: 110.0 parts

Cyclohexanone: 110.0 parts

Polyisocyanate (CORONATE (registered trademark) L manufactured by Tosoh Corporation): 3.0 parts

Preparation Method

A dispersion liquid A was prepared by dispersing (first stage) various components of the magnetic liquid with a batch type vertical sand mill by using zirconia beads having a bead diameter of 0.5 mm (first dispersion beads, density of 6.0 g/cm³) for 24 hours, and then performing filtering with a filter having a hole diameter of 0.5 μm. The used amount of zirconia beads was 10 times of the amount of the ferromagnetic hexagonal ferrite powder based on mass.

After that, a dispersion liquid (dispersion liquid B) was prepared by dispersing (second stage) dispersion liquid A with a batch type vertical sand mill by using diamond beads having a bead diameter shown in Table 6 (second dispersion beads, density of 3.5 g/cm³) for a period of time shown in Table 6, and then separating diamond beads by using a centrifugal separator. The magnetic liquid is the dispersion liquid B obtained as described above.

The magnetic liquid, the abrasive solution, the projection formation agent liquid, and the other components were introduced in a dissolver stirrer and stirred at a circumferential speed of 10 m/sec for a period of time shown in the condition C of Table 5 (stirring time). After that, a ultrasonic dispersion process was performed at a flow rate of 7.5 kg/min with a flow type ultrasonic disperser for a period of time shown in the condition C of Table 5 (ultrasonic dispersion time), and filtering with a filter having a hole diameter shown in the condition C of Table 5 was performed for the number of times shown in the condition C of Table 5, thereby preparing the magnetic layer forming composition.

The activation volume of the ferromagnetic hexagonal ferrite powder described above is a value calculated by performing measurement by using a powder of the powder lot which is the same as that of ferromagnetic hexagonal ferrite powder used in the preparation of the magnetic layer forming composition. The magnetic field sweep rates in the coercivity Hc measurement part at timing points of 3 minutes and 30 minutes were measured by using a vibrating sample magnetometer (manufactured by Toei Industry Co., Ltd.), and the activation volume was calculated from the relational expression described above. The measurement was performed in the environment of 23° C.±1° C.

Preparation of Non-Magnetic Layer Forming Composition

A non-magnetic layer forming composition was prepared by dispersing various components of the non-magnetic layer forming composition with a batch type vertical sand mill by using zirconia beads having a bead diameter of 0.1 mm for 24 hours, and then performing filtering with a filter having a hole diameter of 0.5 μm.

Non-magnetic inorganic powder: α-iron oxide: 100.0 parts

-   -   (Average particle size: 10 nm, BET specific surface area: 75         m²/g) Carbon black: 25.0 parts     -   (Average particle size: 20 nm)

A SO₃Na group-containing polyurethane resin: 18.0 parts

-   -   (Weight-average molecular weight: 70,000, content of SO₃Na         group: 0.2 meq/g)

Stearic acid: 1.0 parts

Cyclohexanone: 300.0 parts

Methyl ethyl ketone: 300.0 parts

Preparation of Back Coating Layer Forming Composition

Components among various components of the back coating layer forming composition except a lubricant (stearic acid and butyl stearate), polyisocyanate, and 200.0 parts of cyclohexanone were kneaded and diluted by an open kneader, and subjected to a dispersion process of 12 passes, with a transverse beads mill disperser and zirconia beads having a bead diameter of 1 mm, by setting a bead filling percentage as 80 volume %, a circumferential speed of rotor distal end as 10 m/sec, and a retention time for 1 pass as 2 minutes. After that, the remaining components were added and stirred with a dissolver, the obtained dispersion liquid was filtered with a filter having a hole diameter of 1 μm and a back coating layer forming composition was prepared.

Non-magnetic inorganic powder: α-iron oxide: 80.0 parts

-   -   (Average particle size: 0.15 μm, BET specific surface area: 52         m²/g) Carbon black: 20.0 parts     -   (Average particle size: 20 nm)

A vinyl chloride copolymer: 13.0 parts

A sulfonic acid salt group-containing polyurethane resin: 6.0 parts

Phenylphosphonic acid: 3.0 parts

Cyclohexanone: 155.0 parts

Methyl ethyl ketone: 155.0 parts

Stearic acid: 3.0 parts

Butyl stearate: 3.0 parts

Polyisocyanate: 5.0 parts

Cyclohexanone: 200.0 parts

Manufacturing of Magnetic Tape

A magnetic tape was manufactured by the specific aspect shown in FIG. 1. The magnetic tape was specifically manufactured as follows.

A support made of polyethylene naphthalate having a thickness of 5.0 μm was sent from the sending part, and the non-magnetic layer forming composition was applied to one surface thereof so that the thickness after the drying becomes 100 nm in the first coating part to form a coating layer. The cooling step was performed by passing the formed coating layer through the cooling zone in which the atmosphere temperature is adjusted to 0° C. for the staying time shown in Table 6 while the coating layer is wet, and then the heating and drying step was performed by passing the coating layer through the first heating process zone at the atmosphere temperature of 100° C., to form a non-magnetic layer.

Then, the magnetic layer forming composition prepared as described above was applied onto the non-magnetic layer so that the thickness after the drying becomes 70 nm in the second coating part, and a coating layer was formed. A homeotropic alignment process was performed in the alignment zone by applying a magnetic field having a magnetic field strength shown in Table 6 to the surface of the coating layer of the magnetic layer forming composition in a vertical direction while the coating layer is wet (not dried), and the coating layer was dried in the second heating process zone (atmosphere temperature of 100° C.).

After that, in the third coating part, the back coating layer forming composition prepared as described above was applied to the surface of the non-magnetic support made of polyethylene naphthalate on a side opposite to the surface where the non-magnetic layer and the magnetic layer are formed, so that the thickness after the drying becomes 0.4 μm, to form a coating layer, and the formed coating layer was dried in a third heating process zone (atmosphere temperature of 100° C.).

After that, a calender process (surface smoothing treatment) was performed with a calender roll configured of only a metal roll, at a speed of 80 m/min, linear pressure of 294 kN/m (300 kg/cm), and a calender temperature (surface temperature of a calender roll) of 90° C.

Then, a heating process was performed in the environment of the atmosphere temperature of 70° C. for 36 hours. After the heating process, the layer was slit to have a width of ½ inches (0.0127 meters), and a servo pattern was formed on the magnetic layer by a commercially available servo writer.

By doing so, a magnetic tape of Example 1 was obtained.

Examples 2 to 9 and Comparative Examples 1 to 14

A magnetic tape was manufactured in the same manner as in Example 1, except that various items shown in Table 5 and Table 6 were changed as shown in each table.

All of the oxide abrasive shown in Table 5 are alumina powder.

In Table 6, in the comparative examples in which “none” is shown in a column of the dispersion beads and a column of the time, the magnetic layer forming composition was prepared without performing the second stage in the magnetic liquid dispersion process.

In Table 6, in the examples in which “none” is shown in a column of the homeotropic alignment process magnetic field strength, the magnetic layer was formed without performing the alignment process.

In Table 6, in the examples in which “not performed” is disclosed in a column of the cooling zone staying time, a magnetic tape was manufactured by a manufacturing step not including the cooling zone in the magnetic layer forming step.

Evaluation of Physical Properties of Magnetic Tape

(1) XRD Intensity Ratio

A tape sample was cut out from the manufactured magnetic tape.

Regarding the cut-out tape sample, the surface of the magnetic layer was irradiated with X-ray by using a thin film X-ray diffraction device (Smart Lab manufactured by Rigaku Corporation), and the In-Plane XRD was performed by the method described above.

The peak intensity Int(114) of the diffraction peak of the (114) plane and the peak intensity Int(110) of the diffraction peak of a (110) plane of a hexagonal ferrite crystal structure were obtained from the X-ray diffraction spectra obtained by the In-Plane XRD, and the XRD intensity ratio (Int(110)/Int(114)) was calculated.

(2) Vertical Squareness Ratio

A vertical squareness ratio of each manufactured magnetic tape was obtained by the method described above using a vibrating sample magnetometer (manufactured by Toei Industry Co., Ltd.).

(3) FIB Abrasive Diameter

The FIB abrasive diameter of each manufactured magnetic tape was obtained by the following method.

As a focused ion beam device, MI4050 manufactured by Hitachi High-Technologies Corporation was used, and the image analysis software, ImageJ which is free software was used.

(i) Acquiring of Secondary Ion Image

The surface of the back coating layer of the sample for measurement cut out from each manufactured magnetic tape was bonded to an adhesive layer of a commercially available carbon double-sided tape for SEM measurement (double-sided tape in which a carbon film is formed on a base material formed of aluminum). An adhesive layer of this double-sided tape on a surface opposite to the surface bonded to the surface of the back coating layer was bonded to a sample table of the focused ion beam device. By doing so, the sample for measurement was disposed on the sample table of the focused ion beam device so that the surface of the magnetic layer faces upwards.

Without performing the coating process before the imaging, the beam setting of the focused ion beam device was set so that an acceleration voltage is 30 kV, a current value is 133 pA, a beam size is 30 nm, and a brightness is 50%, and an SI signal was detected by a secondary ion detector. ACB was carried out at three spots on a non-imaged region of the surface of the magnetic layer to stabilize a color of the image. Then, the contrast reference value and the brightness reference value were determined. The brightness reference value as determined in the above ACB and the contrast value which was lowered by 1% from the contrast reference value as determined in the above ACB were determined as the conditions for capturing a secondary ion image. A non-imaged region of the surface of the magnetic layer was selected and imaging was performed under the conditions for capturing as determined above and at a pixel distance of 25.0 (nm/pixel). As an image capturing method, PhotoScan Dot×4_Dwell Time 15 μsec (capturing time: 1 min), and a capturing size was set as 25 μm×25 μm. By doing so, a secondary ion image of a region of the surface of the magnetic layer having a size of 25 μm×25 μm was obtained. After the scanning, the obtained secondary ion image was stored as a file format, JPEG, by ExportImage, by clicking mouse right button on the captured screen. The pixel number of the image which was 2,000 pixel×2,100 pixel was confirmed, the cross mark and the micron bar on the captured image were deleted, and an image of 2,000 pixel×2,000 pixel was obtained.

(ii) Calculation of FIB Abrasive Diameter

The image data of the secondary ion image obtained in (i) was dragged and dropped in ImageJ which is the image analysis software.

A tone of the image data was changed to 8 bit by using the image analysis software. Specifically, Image of the operation menu of the image analysis software was clicked and 8 bit of Type was selected.

For the binarization process, 250 gradations was selected as a lower limit value, 255 gradations was selected as an upper limit value, and the binarization process was executed by these two threshold values. Specifically, on the operation menu of the image analysis software, Image was clicked, Threshold of Adjust was selected, the lower limit value was selected as 250, the upper limit value was selected as 255, and then, apply was selected. Regarding the obtained image, Process of the operation menu of the image analysis software was clicked, Despeckle of Noise was selected, and Size 4.0-Infinity was set on AnalyzeParticle to remove noise components.

Regarding the binarization process image obtained as described above, AnalyzeParticle was selected from the operation menu of the image analysis software, and the number and Area (unit: Pixel) of white-shining portions on the image were obtained. The area of each white-shining portion on the image was obtained by converting Area (unit: Pixel) into the area by the image analysis software. Specifically, 1 pixel of the image obtained under the imaging conditions corresponded to 0.0125 μm, and accordingly, the area A [μm²] was calculated by an expression, area A=Area pixel×0.0125̂2. By using the area calculated as described above, an equivalent circle diameter L of each white-shining portion was obtained by an expression, equivalent circle diameter L=(A/π)̂(½)×2=L.

The above step was performed four times at different portions (25 μm×25 μm) of the surface of the magnetic layer of the sample for measurement, and the FIB abrasive diameter was calculated from the obtained result by an expression, FIB abrasive diameter=Σ(Li)/Σi.

(4) C—H Derived C Concentration

The X-ray photoelectron spectroscopic analysis was performed regarding the surface of the magnetic layer of the magnetic tape (measurement region: 300 μm×700 μm) by the following method using an ESCA device, and a C—H derived C concentration was calculated from the analysis result.

Analysis and Calculation Method

All of the measurement (i) to (iii) described below were performed under the measurement conditions shown in Table 1.

TABLE 1 Device AXIS-ULTRA manufactured by Shimadzu Corporation Excitation X-ray source Monochromatic Al-Kα ray (output: 15 kV, 20 mA) Analyzer mode Spectrum Lens mode Hybrid (analysis area: 300 μm × 700 μm) Neutralization electron gun ON (used) for charge correction (Charge neutraliser) Light electron extraction angle 10 deg. (angle formed by a detector and a (take-off angle) sample surface)

(i) Wide Scan Measurement

A wide scan measurement (measurement conditions: see Table 2) was performed regarding the surface of the magnetic layer of the magnetic tape with the ESCA device, and the types of the detected elements were researched (qualitative analysis).

TABLE 2 Energy Capturing Number of resolution time integration times Scan range Pass energy (Step) (Dwell) (Sweeps) 0~1200 eV 160 eV 1 eV/step 100 ms/step 5

(ii) Narrow Scan Measurement

All elements detected in (i) described above were subjected to narrow scan measurement (measurement conditions: see Table 3). An atomic concentration (unit: atom %) of each element detected was calculated from a peak area of each element by using software for a data process attached to the device (Vision 2.2.6). Here, the C concentration was also calculated.

TABLE 3 Number of Energy resolution Capturing time integration times Spectra^(Note1)) Scan range Pass energy (Step) (Dwell) (Sweeps)^(Note2)) C1s 276~296 eV 80 eV 0.1 eV/step 100 ms/step 3 Cl2p 190~212 eV 80 eV 0.1 eV/step 100 ms/step 5 N1s 390~410 eV 80 eV 0.1 eV/step 100 ms/step 5 O1s 521~541 eV 80 eV 0.1 eV/step 100 ms/step 3 Fe2p 700~740 eV 80 eV 0.1 eV/step 100 ms/step 3 Ba3d 765~815 eV 80 eV 0.1 eV/step 100 ms/step 3 Al2p  64~84 eV 80 eV 0.1 eV/step 100 ms/step 5 Y3d 148~168 eV 80 eV 0.1 eV/step 100 ms/step 3 P2p 120~140 eV 80 eV 0.1 eV/step 100 ms/step 5 Zr3d 171~191 eV 80 eV 0.1 eV/step 100 ms/step 5 Bi4f 151~171 eV 80 eV 0.1 eV/step 100 ms/step 3 Sn3d 477~502 eV 80 eV 0.1 eV/step 100 ms/step 5 Si2p  90~110 eV 80 eV 0.1 eV/step 100 ms/step 5 S2p 153~173 eV 80 eV 0.1 eV/step 100 ms/step 5 ^(Note1))Spectra shown in Table 3 (element type) are examples, and in a case where an element not shown in Table 3 is detected by the qualitative analysis of the section (i), the same narrow scan measurement is performed in a scan range including entirety of spectra of the elements detected. ^(Note2))The spectra having excellent signal-to-noise ratio (S/N ratio) were measured in a case where the number of integration times is set as three times. However, even in a case where the number of integration times regarding the entirety of spectra is set as five times, the quantitative results are not affected.

(iii) Acquiring of C1s Spectra

The C1s spectra were acquired under the measurement conditions disclosed in Table 4. Regarding the acquired C1s spectra, after correcting a shift (physical shift) due to a sample electrification by using software for a data process attached to the device (Vision 2.2.6), a fitting process (peak resolution) of the C1s spectra was performed by using the software described above. In the peak resolution, the fitting of C1s spectra was performed by a nonlinear least-squares method using a Gauss-Lorentz complex function (Gaussian component: 70%, Lorentz component: 30%), and a percentage (peak area ratio) of the C—H peak occupying the C1 s spectra was calculated. A C—H derived C concentration was calculated by multiplying the calculated C—H peak area ratio by the C concentration acquired in (ii) described above.

TABLE 4 Number of Energy Capturing integration Pass resolution time times Spectra Scan range energy (Step) (Dwell) (Sweeps) C1s 276~296 eV 10 eV 0.1 eV/step 200 ms/step 20

An arithmetical mean of values obtained by performing the above-mentioned process at different positions of the surface of the magnetic layer of the magnetic tape three times is set as a C—H derived C concentration.

Evaluation of Electromagnetic Conversion Characteristics (SNR)

The electromagnetic conversion characteristics of each manufactured magnetic tape were measured with a reel tester having a width of ½ inches (0.0127 meters) to which a head was fixed, by the following method. The following recording and reproducing were performed by sliding the surface of the magnetic layer of the magnetic tape and the head.

A running speed of the magnetic tape (magnetic head/magnetic tape relative speed) was set as 4 m/sec. As a recording head, a metal-in-gap (MIG) head (gap length of 0.15 μm, track width of 1.0 μm) was used, and a recording current was set as an optimal recording current of each magnetic tape. As a reproducing head, a giant-magnetoresistive (GMR) head having an element thickness of 15 nm, a shield interval of 0.1 μm, and a lead width of 0.5 μm was used. A signal was recorded at linear recording density (300 kfci) and a reproducing signal was measured with a spectrum analyzer manufactured by Shibasoku Co., Ltd. A ratio of an output value of a carrier signal and integral noise over whole spectral range was set as an SNR. For the SNR measurement, a part of a signal which is sufficiently stabilized after running of the magnetic tape was used. The SNR was shown in Table 6 as a relative value in a case where the SNR of Comparative Example 1 was set as 0.0 dB. The unit kfci is a unit of linear recording density (cannot be converted into the unit system SI).

Head Element Chipping Amount in GTT

A magnetic head (MR head) used in a tape drive of TS 1140 manufactured by IBM was attached to a reel tester, the magnetic tape having a length of 1000 m of 1 reel was caused to run for 200 passes, by setting a running speed (magnetic head/magnetic tape relative speed) as 4 m/sec while sliding the surface of the magnetic layer and the MR head.

The same running of 200 passes was repeated by replacing the magnetic tape with a new product (1,000 reels of the magnetic tape were used), and the chipping amount of the MR element of the MR head was measured by the following method.

A carbon film was vapor-deposited on the surface of the MR head including a surface slid on the surface magnetic layer by using a vacuum deposition device (JEE-4X manufactured by JEOL), and a platinum film was formed by sputtering on this carbon film by using an ion sputtering device (E-1030 manufactured by Hitachi High-Technologies Corporation. After that, a cross section parallel to the sliding direction of the magnetic tape in a case of running, was exposed from the MR head by using A FIB-SEM combined machine, Helios 400S manufactured by MRFEI, and a sample for cross section observation (piece having a thickness of 100 nm) was cut out so that the MR element was included in the cross section. A distance in a vertical direction between the sliding surface of the surface of the magnetic layer and the top of the MR element was obtained by using a TEM image obtained by observing the sample for cross section observation using a transmission electron microscope (TEM) (Titan 80-300 manufactured by FEI) at an acceleration voltage of 300 kV. A difference between the obtained distance and a distance obtained by the same method regarding unused MR head was shown as the head element chipping amount in GTT in Table 6.

TABLE 5 Conditions A B C D E F Preparation Oxide abrasive product name Hit80 Hit80 Hit80 Hit100 Hit70 Hit80 of abrasive (manufactured by solution Sumitomo Chemical Co., Ltd.) Oxide abrasive BET 30  30  30  40  20  30  specific surface area (m2/g) Content of abrasive solution 3.0 parts 0 part 3.0 parts 3.0 parts 3.0 parts 3.0 parts dispersing agent (2,3-dihydroxynaphthalene) Beads dispersion time 5 min 60 min 60 min 180 min 60 min 180 min Centrifugal Rotation rate None 3500 rpm 3500 rpm 3500 rpm 5500 rpm 3500 rpm separation Centrifugal None 4 min 4 min 4 min 4 min 4 min separation time Filter hole diameter 0.5 μm 0.3 μm 0.3 μm 0.3 μm 0.3 μm 0.3 μm Preparation of Stirring time 30 min 60 min 360 min 360 min 180 min 360 min magnetic layer Ultrasonic dispersion time 0.5 min 60 min 60 min 60 min 60 min 60 min forming Filter hole diameter 0.5 μm 0.3 μm 0.3 μm 0.3 μm 0.3 μm 0.3 μm composition Number of times of filter process 1 2 3 3 2 3

TABLE 6 Magnetic liquid dispersion process second stage Dispersion beads Preparation condition Used amount (mass of beads Homeotropic of abrasive solution Bead with respect to mass of ferro- alignment process and magnetic layer Kind diameter magnetic hexagonal ferrite powder) Time magnetic field strength forming composition Comparative None None None None None A Example 1 Comparative None None None None None B Example 2 Comparative None None None None None C Example 3 Comparative None None None None None D Example 4 Comparative Diamond 500 nm 10 times 1 h 0.15 T C Example 5 Comparative Diamond 500 nm 10 times 1 h 0.15 T C Example 6 Comparative Diamond 500 nm 10 times 1 h 0.15 T A Example 7 Comparative Diamond 500 nm 10 times 1 h 0.15 T B Example 8 Comparative Diamond 500 nm 10 times 1 h 0.15 T D Example 9 Comparative None None None None None C Example 10 Comparative None None None None 0.15 T C Example 11 Comparative None None None None 0.30 T C Example 12 Comparative Diamond 500 nm 10 times 1 h 1.00 T C Example 13 Comparative Diamond 500 nm 10 times 1 h None C Example 14 Example 1 Diamond 500 nm 10 times 1 h 0.15 T C Example 2 Diamond 500 nm 10 times 1 h 0.20 T C Example 3 Diamond 500 nm 10 times 1 h 0.30 T C Example 4 Diamond 500 nm 10 times 1 h 0.50 T C Example 5 Diamond 500 nm 20 times 1 h 0.15 T C Example 6 Diamond 500 nm 10 times 1 h 0.30 T E Example 7 Diamond 500 nm 10 times 1 h 0.30 T F Example 8 Diamond 500 nm 10 times 1 h 0.30 T C Example 9 Diamond 500 nm 10 times 1 h 0.30 T C Head element Vertical chipping amount Cooling zone C—H derived C XRD intensity ratio squareness FIB abrasive SNR in GTT staying time concentration Int(110)/Int(114) ratio diameter (dB) (nm) Comparative Not performed 35 atom % 0.2 0.55 0.16 μm 0.0 10.0 Example 1 Comparative Not performed 35 atom % 0.2 0.55 0.11 μm 1.0 7.0 Example 2 Comparative Not performed 35 atom % 0.2 0.55 0.06 μm 2.0 4.0 Example 3 Comparative Not performed 35 atom % 0.2 0.55 0.03 μm 2.9 6.0 Example 4 Comparative Not performed 35 atom % 0.5 0.70 0.06 μm 5.0 4.0 Example 5 Comparative 180 seconds 70 atom % 0.5 0.70 0.06 μm 5.1 4.0 Example 6 Comparative 1 second 45 atom % 0.5 0.70 0.16 μm 3.0 9.0 Example 7 Comparative 1 second 45 atom % 0.5 0.70 0.11 μm 3.9 6.1 Example 8 Comparative 1 second 45 atom % 0.5 0.70 0.03 μm 6.0 7.9 Example 9 Comparative 1 second 45 atom % 0.2 0.55 0.06 μm 2.0 0.0 Example 10 Comparative 1 second 45 atom % 3.8 0.63 0.06 μm 2.1 0.0 Example 11 Comparative 1 second 45 atom % 5.0 0.75 0.06 μm 2.1 0.0 Example 12 Comparative 1 second 45 atom % 6.1 0.90 0.06 μm 2.1 0.0 Example 13 Comparative 1 second 45 atom % 0.3 0.66 0.06 μm 2.0 0.0 Example 14 Example 1 1 second 45 atom % 0.5 0.70 0.06 μm 5.1 0.0 Example 2 1 second 45 atom % 1.5 0.75 0.06 μm 5.0 0.0 Example 3 1 second 45 atom % 2.3 0.80 0.06 μm 5.0 0.0 Example 4 1 second 45 atom % 4.0 0.85 0.06 μm 5.1 0.0 Example 5 1 second 45 atom % 0.7 0.83 0.06 um 5.1 0.0 Example 6 1 second 45 atom % 2.3 0.80 0.08 μm 5.6 0.0 Example 7 1 second 45 atom % 2.3 0.80 0.04 μm 5.4 0.0 Example 8 5 seconds 55 atom % 2.3 0.80 0.06 μm 5.0 0.0 Example 9 50 seconds 65 atom % 2.3 0.80 0.06 μm 5.0 0.0

From the results shown in Table 6, it is possible to confirm that, in Examples 1 to 9 in which the XRD intensity ratio of the magnetic tape, the vertical squareness ratio, the C—H derived C concentration of the magnetic layer, and the FIB abrasive diameter are in the ranges described above, the reproduction can be performed at a high SNR (that is, excellent electromagnetic conversion characteristics can be exhibited) and the occurrence of the head element chipping in GTT is prevented. It is thought that, in Comparative Example 7 and Comparative Example 8, a reason of a decrease in SNR compared to that in Examples 1 to 9, is due to an increase in distance between the surface of the magnetic layer and the reproducing element and the occurrence of spacing loss, due to the coarse surface of the magnetic layer, caused by the oxide abrasive present in the magnetic layer in a state where the FIB abrasive diameter significantly exceeds 0.08 μm.

One aspect of the invention is effective in a technical field of a magnetic recording medium used as a recording medium for archive. 

What is claimed is:
 1. A magnetic recording medium comprising: a non-magnetic support; and a magnetic layer, wherein the magnetic layer comprises a ferromagnetic powder, a binding agent and an oxide abrasive, the ferromagnetic powder is a ferromagnetic hexagonal ferrite powder, an intensity ratio Int(110)/Int(114) of a peak intensity Int(110) of a diffraction peak of a (110) plane with respect to a peak intensity Int(114) of a diffraction peak of a (114) plane of a hexagonal ferrite crystal structure obtained by an X-ray diffraction analysis of the magnetic layer by using an In-Plane method is 0.5 to 4.0, a vertical squareness ratio of the magnetic recording medium is 0.65 to 1.00, one or more kinds of component selected from the group consisting of fatty acid and fatty acid amide is contained in a magnetic layer side portion on the non-magnetic support, a C—H derived C concentration calculated from a C—H peak area ratio of C1s spectra obtained by X-ray photoelectron spectroscopic analysis performed on the surface of the magnetic layer at a photoelectron take-off angle of 10 degrees is 45 atom % to 65 atom %, and an average particle diameter of the oxide abrasive obtained from a secondary ion image obtained by irradiating the surface of the magnetic layer with a focused ion beam is 0.04 μm to 0.08 μm.
 2. The magnetic recording medium according to claim 1, wherein the vertical squareness ratio is 0.65 to 0.90.
 3. The magnetic recording medium according to claim 1, wherein the oxide abrasive is an alumina powder.
 4. The magnetic recording medium according to claim 1, further comprising: a non-magnetic layer including a non-magnetic powder and a binding agent between the non-magnetic support and the magnetic layer.
 5. The magnetic recording medium according to claim 1, further comprising: a back coating layer including a non-magnetic powder and a binding agent on a surface of the non-magnetic support opposite to a surface provided with the magnetic layer.
 6. The magnetic recording medium according to claim 1, which is a magnetic tape.
 7. A magnetic recording and reproducing device comprising: a magnetic recording medium; and a magnetic head, wherein the magnetic recording medium is a magnetic recording medium comprising: a non-magnetic support; and a magnetic layer, wherein the magnetic layer comprises a ferromagnetic powder, a binding agent and an oxide abrasive, the ferromagnetic powder is a ferromagnetic hexagonal ferrite powder, an intensity ratio Int(110)/Int(114) of a peak intensity Int(110) of a diffraction peak of a (110) plane with respect to a peak intensity Int(114) of a diffraction peak of a (114) plane of a hexagonal ferrite crystal structure obtained by an X-ray diffraction analysis of the magnetic layer by using an In-Plane method is 0.5 to 4.0, a vertical squareness ratio of the magnetic recording medium is 0.65 to 1.00, one or more kinds of component selected from the group consisting of fatty acid and fatty acid amide is contained in a magnetic layer side portion on the non-magnetic support, a C—H derived C concentration calculated from a C—H peak area ratio of C1s spectra obtained by X-ray photoelectron spectroscopic analysis performed on the surface of the magnetic layer at a photoelectron take-off angle of 10 degrees is 45 atom % to 65 atom %, and an average particle diameter of the oxide abrasive obtained from a secondary ion image obtained by irradiating the surface of the magnetic layer with a focused ion beam is 0.04 μm to 0.08 μm.
 8. The magnetic recording and reproducing device according to claim 7, wherein the magnetic head is a magnetic head including magnetoresistive element.
 9. The magnetic recording and reproducing device according to claim 7, wherein the vertical squareness ratio is 0.65 to 0.90.
 10. The magnetic recording and reproducing device according to claim 7, wherein the oxide abrasive is an alumina powder.
 11. The magnetic recording and reproducing device according to claim 7, wherein the magnetic recording medium comprises a non-magnetic layer including a non-magnetic powder and a binding agent between the non-magnetic support and the magnetic layer.
 12. The magnetic recording and reproducing device according to claim 7, wherein the magnetic recording medium comprises a back coating layer including a non-magnetic powder and a binding agent on a surface of the non-magnetic support opposite to a surface provided with the magnetic layer.
 13. The magnetic recording and reproducing device according to claim 7, wherein the magnetic recording medium is a magnetic tape. 